High transmission glasses with alkaline earth oxides as a modifier

ABSTRACT

Compounds, compositions, articles, devices, and methods for the manufacture of light guide plates and back light units including such light guide plates made from glass. In some embodiments, light guide plates (LGPs) are provided that have similar or superior optical properties to light guide plates made from PMMA and that have exceptional mechanical properties such as rigidity, CTE and dimensional stability in high moisture conditions as compared to PMMA light guide plates.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a national stage entry of International Patent Application Serial No. PCT/US2017/051483, filed on Sep. 14, 2017, which in turn, claims the benefit of priority under 35 U.S.C. § 119 of U.S. Provisional Application Ser. No. 62/395,406 filed on Sep. 16, 2016, the contents of each of which are is relied upon and incorporated herein by reference in their entireties.

BACKGROUND

Side lit back light units include a light guide plate (LGP) that is usually made of high transmission plastic materials such as polymethylmethacrylate (PMMA). Although such plastic materials present excellent properties such as light transmission, these materials exhibit relatively poor mechanical properties such as rigidity, coefficient of thermal expansion (CTE) and moisture absorption.

Accordingly, it would be desirable to provide an improved light guide plate having attributes that achieve an improved optical performance in terms of light transmission, solarization, scattering and light coupling as well as exhibiting exceptional mechanical performance in terms of rigidity, CTE, and moisture absorption.

Further, it would be desirable to provide the above attributes and performance using less expensive raw materials, to reduce blisters in the manufacturing process, and to increase flow in the manufacturing process.

SUMMARY

Aspects of the subject matter pertain to compounds, compositions, articles, devices, and methods for the manufacture of light guide plates and back light units including such light guide plates made from glass. In some embodiments, light guide plates (LGPs) are provided that have similar or superior optical properties to light guide plates made from PMMA and that have exceptional mechanical properties such as rigidity, CTE and dimensional stability in high moisture conditions as compared to PMMA light guide plates.

Principles and embodiments of the present subject matter relate in some embodiments to a light guide plate for use in a backlight unit. In some embodiments the light guide plate or glass article can comprise a glass sheet with a front face having a width and a height, a back face opposite the front face, and a thickness between the front face and back face, forming four edges around the front and back faces, wherein the glass sheet comprises between about 74 mol % to about 77 mol % SiO₂, between about 3 mol % to about 6 mol % Al₂O₃, between about 0 mol % to about 3.5 mol % B₂O₃, between about 4 mol % to about 7 mol % R₂O, wherein R is any one or more of Li, Na, K, Rb, Cs, between about 11 mol % to about 16 mol % RO, wherein R is any one or more of Mg, Ca, Sr or Ba, between about 0 mol % to about 4 mol % ZnO, and between about 0 mol % to about 1.7 mol % ZrO₂. In some embodiments, the glass has a color shift<0.005. In some embodiments, the glass has a strain temperature greater than about 600° C. In some embodiments, the glass has an annealing temperature greater than about 650° C. In some embodiments, the glass has a CTE between about 55×10−7/° C. and about 64×10−7/° C. In some embodiments, the glass has a density between about 2.51 gm/cc @ 20 C and about 2.64 gm/cc @ 20 C. In some embodiments, the glass article is a light guide plate. In some embodiments, the thickness of the plate is between about 0.2 mm and about 8 mm. In some embodiments, the light guide plate is manufactured from a fusion draw process, slot draw process, or a float process. In some embodiments, the glass comprises less than about 20 ppm each of Co, Ni, and Cr. In some embodiments, the glass comprises less than about 20 ppm total of Co, Ni, and Cr. In some embodiments, the glass comprises less than about 20 ppm of Fe, less than about 5 ppm of Co, and less than about 5 ppm of Ni. In some embodiments, Al₂O₃/R₂O<1. In some embodiments, Al₂O₃ is substantially equal to R₂O+/−0.05. In some embodiments, the glass does not contain BaO and the mol % of SrO, MgO and CaO are within 1.0 mol % of each other. In some embodiments, the glass contains BaO and the mol % of SrO, BaO, MgO and CaO are within 1.0 mol % of each other. In some embodiments, the T35 kP temperature is greater than or equal to 1200° C. In some embodiments, the T200 P temperature is less than or equal to 1700° C. In some embodiments, the transmittance at 450 nm with at least 500 mm in length is greater than or equal to 85%, the transmittance at 550 nm with at least 500 mm in length is greater than or equal to 90%, or the transmittance at 630 nm with at least 500 mm in length is greater than or equal to 85%, and combinations thereof. In some embodiments, the glass sheet is chemically strengthened. In some embodiments, R₂O/RO is between about 0.3 to less than about 1.0. In some embodiments, R₂O/RO is between about 0.38 to about 0.53. In some embodiments, Al₂O₃—R₂O is between −2 and 0.5.

In other embodiments, a glass article is provided comprising a glass sheet with a front face having a width and a height, a back face opposite the front face, and a thickness between the front face and back face, forming four edges around the front and back faces, wherein the glass sheet comprises greater than about 74 mol % SiO₂, between about 3 mol % to about 6 mol % Al₂O₃, between about 0 mol % to about 3.5 mol % B₂O₃, between about 4 mol % to about 7 mol % R₂O, wherein R is any one or more of Li, Na, K, Rb, Cs, wherein Al₂O₃—R₂O is between about −2 and about 0.5. In further embodiments, a glass article is provided comprising a glass sheet with a front face having a width and a height, a back face opposite the front face, and a thickness between the front face and back face, forming four edges around the front and back faces, wherein the glass sheet comprises greater than about 74 mol % SiO₂, between about 3 mol % to about 6 mol % Al₂O₃, between about 0 mol % to about 3.5 mol % B₂O₃, between about 4 mol % to about 7 mol % R₂O, wherein R is any one or more of Li, Na, K, Rb, Cs, between about 11 mol % to about 16 mol % RO, wherein R is any one or more of Mg, Ca, Sr or Ba, wherein R₂O/RO is between about 0.3 to less than about 1.0. In some embodiments, R₂O/RO is between about 0.38 to about 0.53. In some embodiments, the glass has a color shift<0.005. In some embodiments, the glass has a strain temperature greater than about 600° C. In some embodiments, the glass has an annealing temperature greater than about 650° C. In some embodiments, the glass has a CTE between about 55×10−7/° C. and about 64×10−7/° C. In some embodiments, the glass has a density between about 2.51 gm/cc @ 20 C and about 2.64 gm/cc @ 20 C. In some embodiments, the glass article is a light guide plate. In some embodiments, the thickness of the plate is between about 0.2 mm and about 8 mm. In some embodiments, the light guide plate is manufactured from a fusion draw process, slot draw process, or a float process. In some embodiments, the glass comprises less than about 20 ppm each of Co, Ni, and Cr. In some embodiments, the glass comprises less than about 20 ppm total of Co, Ni, and Cr. In some embodiments, the glass comprises less than about 20 ppm of Fe, less than 5 ppm of Co, and less than 5 ppm of Ni. In some embodiments, Al₂O₃/R₂O<1. In some embodiments, Al₂O₃ is substantially equal to R₂O+/−0.05. In some embodiments, the transmittance at 450 nm with at least 500 mm in length is greater than or equal to 85%, the transmittance at 550 nm with at least 500 mm in length is greater than or equal to 90%, or the transmittance at 630 nm with at least 500 mm in length is greater than or equal to 85%, and combinations thereof.

In yet further embodiments, a glass article is provided comprising a glass sheet with a front face having a width and a height, a back face opposite the front face, and a thickness between the front face and back face, forming four edges around the front and back faces, wherein the glass sheet comprises greater than about 74 mol % SiO₂, between about 3 mol % to about 6 mol % Al₂O₃, between about 0 mol % to about 3.5 mol % B₂O₃, between about 4 mol % to about 7 mol % R₂O, wherein R is any one or more of Li, Na, K, Rb, Cs, between about 11 mol % to about 16 mol % RO, wherein R is any one or more of Mg, Ca, Sr or Ba, wherein Al₂O₃—R₂O is between about −2 and about 0.5, and wherein R₂O/RO is between about 0.3 to less than about 1.0. In some embodiments, R₂O/RO is between about 0.38 to about 0.53. In some embodiments, the glass has a color shift<0.005. In some embodiments, the glass article is a light guide plate. In some embodiments, the glass comprises less than about 20 ppm each of Co, Ni, and Cr. In some embodiments, the glass comprises less than about 20 ppm total of Co, Ni, and Cr. In some embodiments, the glass comprises less than about 20 ppm of Fe, less than 5 ppm of Co, and less than 5 ppm of Ni.

Additional features and advantages of the disclosure will be set forth in the detailed description which follows, and in part will be readily apparent to those skilled in the art from that description or recognized by practicing the methods as described herein, including the detailed description which follows, the claims, as well as the appended drawings.

It is to be understood that both the foregoing general description and the following detailed description present various embodiments of the disclosure, and are intended to provide an overview or framework for understanding the nature and character of the claims. The accompanying drawings are included to provide a further understanding of the disclosure, and are incorporated into and constitute a part of this specification. The drawings illustrate various embodiments of the disclosure and together with the description serve to explain the principles and operations of the disclosure.

BRIEF DESCRIPTION OF THE DRAWINGS

The following detailed description can be further understood when read in conjunction with the following drawings.

FIG. 1 is a pictorial illustration of an exemplary embodiment of a light guide plate;

FIG. 2 is a graph showing percentage light coupling versus distance between an LED and LGP edge;

FIG. 3 is a graph showing the estimated light leakage in dB/m versus RMS roughness of an LGP;

FIG. 4 is a graph showing an expected coupling (without Fresnel losses) as a function of distance between the LGP and LED for a 2 mm thick LED's coupled into a 2 mm thick LGP;

FIG. 5 is a pictorial illustration of a coupling mechanism from an LED to a glass LGP;

FIG. 6 is a graph showing an expected angular energy distribution calculated from surface topology;

FIG. 7 is a pictorial illustration showing total internal reflection of light at two adjacent edges of a glass LGP;

FIG. 8 is a cross sectional illustration of an exemplary LCD panel with a LGP in accordance with one or more embodiments;

FIG. 9 is a cross sectional illustration of an exemplary LCD panel with a LGP according to another embodiment;

FIG. 10 is a pictorial illustration showing an LGP with adhesion pads according to additional embodiments;

FIG. 11 is a graph depicting transmission values of exemplary glass compositions doped individually with Fe₂O₃, NiO, and Cr₂O₃;

FIG. 12 is a graph depicting transmission values of exemplary glass compositions with varied R₂O types;

FIG. 13 is a graph depicting transmission values for glasses in Table 2;

FIG. 14 is a graph depicting transmission values for glasses having varied alkaline earths;

FIGS. 15A and 15B are graphs depicting transmission values for glasses with and without boron and with a varied Al₂O₃ and R₂O content; and

FIGS. 16A and 16 B are graphs depicting transmission values for glasses in Tables 5 and 6.

DETAILED DESCRIPTION

Described herein are light guide plates, methods of making light guide plates and backlight units utilizing light guide plates in accordance with embodiments of the present invention.

Current light guide plates used in LCD backlight applications are typically made from PMMA material since this is one of the best materials in term of optical transmission in the visible spectrum. However, PMMA presents mechanical problems that make large size (e.g., 50 inch diagonal and greater) displays challenging in term of mechanical design, such as, rigidity, moisture absorption, and coefficient of thermal expansion (CTE).

With regard to rigidity, conventional LCD panels are made of two pieces of thin glass (color filter substrate and TFT substrate) with a PMMA light guide and a plurality of thin plastic films (diffusers, dual brightness enhancement films (DBEF) films, etc.). Due to the poor elastic modulus of PMMA, the overall structure of the LCD panel does not have sufficient rigidity, and additional mechanical structure is necessary to provide stiffness for the LCD panel. It should be noted that PMMA generally has a Young's modulus of about 2 GPa, while certain exemplary glasses have a Young's modulus ranging from about 60 GPa to 90 GPa or more.

Regarding moisture absorption, humidity testing shows that PMMA is sensitive to moisture and size can change by about 0.5%. For a PMMA panel having a length of one meter, this 0.5% change can increase the length by 5 mm, which is significant and makes the mechanical design of a corresponding backlight unit challenging. Conventional means to solve this problem is leaving an air gap between the light emitting diodes (LEDs) and the PMMA light guide plate (LGP) to let the material expand. A problem with this approach is that light coupling is extremely sensitive to the distance from the LEDs to the LGP, which can cause the display brightness to change as a function of humidity. FIG. 2 is a graph showing percentage light coupling versus distance between an LED and LGP edge. With reference to FIG. 2, a relationship is shown which illustrates the drawbacks of conventional measures to solve challenges with PMMA. More specifically, FIG. 2 illustrates a plot of light coupling versus LED to LGP distance assuming both are 2 mm in height. It can be observed that the further the distance between LED and LGP, a less efficient light coupling is made between the LED and LGP.

With regard to CTE, the CTE of PMMA is about 75E−6 C⁻¹ and has relatively low thermal conductivity (0.2 W/m/K) while some glasses have a CTE of about 8E−6 C⁻¹ and a thermal conductivity of 0.8 W/m/K. Of course, the CTE of other glasses can vary and such a disclosure should not limit the scope of the claims appended herewith. PMMA also has a transition temperature of about 105° C., and when used an LGP, a PMMA LGP material can become very hot whereby its low conductivity makes it difficult to dissipate heat. Accordingly, using glass instead of PMMA as a material for light guide plates provides benefits in this regard, but conventional glass has a relatively poor transmission compared to PMMA due mostly to iron and other impurities. Also some other parameters such as surface roughness, waviness, and edge quality polishing can play a significant role on how a glass light guide plate can perform. According embodiments of the invention, glass light guide plates for use in backlight units can have one or more of the following attributes.

Glass Light Guide Plate Structure and Composition

FIG. 1 is a pictorial illustration of an exemplary embodiment of a light guide plate. With reference to FIG. 1, an illustration is provided of an exemplary embodiment having a shape and structure of an exemplary light guide plate comprising a sheet of glass having a first face 110, which may be a front face, and a second face opposite the first face, which may be a back face. The first and second faces may have a height, H, and a width, W. The first and/or second face(s) may have a roughness that is less than 0.6 nm, less than 0.5 nm, less than 0.4 nm, less than 0.3 nm, less than 0.2 nm, less than 0.1 nm, or between about 0.1 nm and about 0.6 nm.

The glass sheet may have a thickness, T, between the front face and the back face, where the thickness forms four edges. The thickness of the glass sheet may be less than the height and width of the front and back faces. In various embodiments, the thickness of the plate may be less than 1.5% of the height of the front and/or back face. Alternatively, the thickness, T, may be less than about 3 mm, less than about 2 mm, less than about 1 mm, or between about 0.1 mm to about 3 mm. The height, width, and thickness of the light guide plate may be configured and dimensioned for use in an LCD backlight application.

A first edge 130 may be a light injection edge that receives light provided for example by a light emitting diode (LED). The light injection edge may scatter light within an angle less than 12.8 degrees full width half maximum (FWHM) in transmission. The light injection edge may be obtained by grinding the edge without polishing the light injection edge. The glass sheet may further comprise a second edge 140 adjacent to the light injection edge and a third edge opposite the second edge and adjacent to the light injection edge, where the second edge and/or the third edge scatter light within an angle of less than 12.8 degrees FWHM in reflection. The second edge 140 and/or the third edge may have a diffusion angle in reflection that is below 6.4 degrees. It should be noted that while the embodiment depicted in FIG. 1 shows a single edge 130 injected with light, the claimed subject matter should not be so limited as any one or several of the edges of an exemplary embodiment 100 can be injected with light. For example, in some embodiments, the first edge 130 and its opposing edge can both be injected with light. Such an exemplary embodiment may be used in a display device having a large and or curvilinear width W. Additional embodiments may inject light at the second edge 140 and its opposing edge rather than the first edge 130 and/or its opposing edge. Thicknesses of exemplary display devices can be less than about 10 mm, less than about 9 mm, less than about 8 mm, less than about 7 mm, less than about 6 mm, less than about 5 mm, less than about 4 mm, less than about 3 mm, or less than about 2 mm.

In various embodiments, the glass composition of the glass sheet may comprise between 74-77 mol % SiO₂, between 3-6 mol % Al₂O₃, and between 0-4 mol % B₂O₃, and less than 50 ppm iron (Fe) concentration. In some embodiments, there may be less than 25 ppm Fe, or in some embodiments the Fe concentration may be about 20 ppm or less. In various embodiments, the thermal conduction of the light guide plate 100 may be greater than 0.5 W/m/K. In additional embodiments, the glass sheet may be formed by a polished float glass, a fusion draw process, a slot draw process, a redraw process, or another suitable forming process.

According to one or more embodiments, the LGP can be made from a glass comprising colorless oxide components selected from the glass formers SiO₂, Al₂O₃, and B₂O₃. The exemplary glass may also include fluxes to obtain favorable melting and forming attributes. Such fluxes include alkali oxides (Li₂O, Na₂O, K₂O, Rb₂O and Cs₂O) and alkaline earth oxides (MgO, CaO, SrO, ZnO and BaO). In one embodiment, the glass contains constituents in the range of 74-77 mol % SiO₂, in the range of 3-6 mol % Al₂O₃, in the range of 0-4 mol % B₂O₃, and in the range of 4 to 7% alkali oxides, 10 to 16% alkaline earth oxides, or combinations thereof.

In some glass compositions described herein, SiO₂ can serve as the basic glass former. In certain embodiments, the concentration of SiO₂ can be greater than 60 mole percent to provide the glass with a density and chemical durability suitable for a display glasses or light guide plate glasses, and a liquidus temperature (liquidus viscosity), which allows the glass to be formed by a downdraw process (e.g., a fusion process). In terms of an upper limit, in general, the SiO₂ concentration can be less than or equal to about 80 mole percent to allow batch materials to be melted using conventional, high volume, melting techniques, e.g., Joule melting in a refractory melter. As the concentration of SiO₂ increases, the 200 poise temperature (melting temperature) generally rises. In various applications, the SiO₂ concentration is adjusted so that the glass composition has a melting temperature less than or equal to 1,750° C. In various embodiments, the mol % of SiO₂ may be in the range of about 73 to about 77 mol %, or alternatively in the range of about 74 to about 76 mol %, and all subranges therebetween.

Al₂O₃ is another glass former used to make the glasses described herein. Higher mole percent Al₂O₃ can improve the glass's annealing point and modulus. In various embodiments, the mol % of Al₂O₃ may be in the range of about 3 to about 6 mol %, or alternatively in the range of about 4 to about 6 mol %, or in the range of about 5 to about 6 mol %, and all subranges there between. In other embodiments, the mol % of Al₂O₃ may be about 5 to 6 mol %, or from 0 to about 5 mol % or from 0 to about 2 mol %, or less than about 6 mol %, or less than about 5 mol %.

B₂O₃ is both a glass former and a flux that aids melting and lowers the melting temperature. It has an impact on both liquidus temperature and viscosity. Increasing B₂O₃ can be used to increase the liquidus viscosity of a glass. To achieve these effects, the glass compositions of one or more embodiments may have B₂O₃ concentrations that are equal to or greater than 0.1 mole percent; however, some compositions may have a negligible amount of B₂O₃. As discussed above with regard to SiO₂, glass durability is very important for display applications. Durability can be controlled somewhat by elevated concentrations of alkaline earth oxides, and significantly reduced by elevated B₂O₃ content. Annealing point decreases as B₂O₃ increases, so it may be helpful to keep B₂O₃ content low. Thus, in various embodiments, the mol % of B₂O₃ may be in the range of about 0% to about 4%, or alternatively in the range of about 0% to about 3%, or in the range of about 0% to about 2%, in the range of about 1% to about 4%, or in the range of about 2% to about 4%, and all subranges there between.

In addition to the glass formers (SiO₂, Al₂O₃, and B₂O₃), the glasses described herein also include alkaline earth oxides. In one embodiment, at least three alkaline earth oxides are part of the glass composition, e.g., MgO, CaO, and BaO, and, optionally, SrO. The alkaline earth oxides provide the glass with various properties important to melting, fining, forming, and ultimate use.

For certain embodiments of this disclosure, the alkaline earth oxides may be treated as what is in effect a single compositional component. This is because their impact upon viscoelastic properties, liquidus temperatures and liquidus phase relationships are qualitatively more similar to one another than they are to the glass forming oxides SiO₂, Al₂O₃ and B₂O₃. However, the alkaline earth oxides CaO, SrO and BaO can form feldspar minerals, notably anorthite (CaAl₂Si₂O₈) and celsian (BaAl₂Si₂O₈) and strontium-bearing solid solutions of same, but MgO does not participate in these crystals to a significant degree. Therefore, when a feldspar crystal is already the liquidus phase, a superaddition of MgO may serves to stabilize the liquid relative to the crystal and thus lower the liquidus temperature. At the same time, the viscosity curve typically becomes steeper, reducing melting temperatures while having little or no impact on low-temperature viscosities.

The inventors have found that the addition of small amounts of MgO may benefit melting by reducing melting temperatures, forming by reducing liquidus temperatures and increasing liquidus viscosity, while preserving high annealing points. In various embodiments, the glass composition comprises MgO in an amount in the range of about 0 mol % to about 6 mol %, or in the range of about 2 mol % to about 4 mol %, or in the range of about 1 mol % to about 5 mol %, or in the range of about 2 mol % to about 5 mol %, or in the range of about 3 mol % to about 5 mol %, and all subranges therebetween.

Without being bound by any particular theory of operation, it is believed that calcium oxide present in the glass composition can produce low liquidus temperatures (high liquidus viscosities), high annealing points and moduli, and CTE's in the most desired ranges for display and light guide plate applications. It also contributes favorably to chemical durability, and compared to other alkaline earth oxides, it is relatively inexpensive as a batch material. However, at high concentrations, CaO increases the density and CTE. Furthermore, at sufficiently low SiO₂ concentrations, CaO may stabilize anorthite, thus decreasing liquidus viscosity. Accordingly, in one or more embodiment, the CaO concentration can be between 2 and 5 mol %. In various embodiments, the CaO concentration of the glass composition is in the range of about 2 mol % to about 4.5 mol %, or in the range of about 2.4 mol % to about 4.5 mol %, and all subranges therebetween.

SrO and BaO can both contribute to low liquidus temperatures (high liquidus viscosities). The selection and concentration of these oxides can be selected to avoid an increase in CTE and density and a decrease in modulus and annealing point. The relative proportions of SrO and BaO can be balanced so as to obtain a suitable combination of physical properties and liquidus viscosity such that the glass can be formed by a downdraw process. In various embodiments, the glass comprises SrO in the range of about 2 to about 6 mol %, or between about 2 mol % to about 5.5 mol %, or about 2.5 to about 5 mol %, 3 mol % to about 5 mol %, and all subranges therebetween. In one or more embodiments, the glass comprises BaO in the range of about 0 to about 5 mol %, or between 1 to about 4 mol %, or between 0 to about 4 mol %, and all subranges therebetween.

In addition to the above components, the glass compositions described herein can include various other oxides to adjust various physical, melting, fining, and forming attributes of the glasses. Examples of such other oxides include, but are not limited to, TiO₂, MnO, V₂O₃, Fe₂O₃, ZrO₂, ZnO, Nb₂O₅, MoO₃, Ta₂O₅, WO₃, Y₂O₃, La₂O₃ and CeO₂ as well as other rare earth oxides and phosphates. In one embodiment, the amount of each of these oxides can be less than or equal to 2.0 mole percent, and their total combined concentration can be less than or equal to 5.0 mole percent. In some embodiments, the glass composition comprises ZnO in an amount in the range of about 0 to about 3.5 mol %, or about 0 to about 3.01 mol %, or about 0 to about 2.0 mol %, and all subranges therebetween. In other embodiments, the glass composition comprises from about 0.1 mol % to about 1.0 mol % titanium oxide; from about 0.1 mol % to about 1.0 mol % zirconium oxide; from about 0.1 mol % to about 1.0 mol % tin oxide; from about 0.1 mol % to about 1.0 mol % molybdenum oxide; from about 0.1 mol % to about 1.0 mol % cerium oxide; and all subranges therebetween of any of the above listed transition metal oxides. The glass compositions described herein can also include various contaminants associated with batch materials and/or introduced into the glass by the melting, fining, and/or forming equipment used to produce the glass. The glasses can also contain SnO₂ either as a result of Joule melting using tin-oxide electrodes and/or through the batching of tin containing materials, e.g., SnO₂, SnO, SnCO₃, SnC₂O₂, etc.

The glass compositions described herein can contain some alkali constituents, e.g., these glasses are not alkali-free glasses. As used herein, an “alkali-free glass” is a glass having a total alkali concentration which is less than or equal to 0.1 mole percent, where the total alkali concentration is the sum of the Na₂O, K₂O, and Li₂O concentrations. In some embodiments, the glass comprises Li₂O in the range of about 0 to about 3.0 mol %, in the range of about 0 to about 2.0 mol %, in the range of about 0 to about 1.0 mol %, and all subranges therebetween. In other embodiments, the glass comprises Na₂O in the range of about 0 mol % to about 5 mol %, in the range of about 0 mol % to about 4 mol %, in the range of about 0 to about 3 mol %, in the range of about 0.1 to about 3 mol %, and all subranges therebetween. In some embodiments, the glass comprises K₂O in the range of about 2 to about 8.0 mol %, in the range of about 2 to about 7.0 mol %, in the range of about 2.5 to about 7.0 mol %, and all subranges therebetween. In exemplary embodiments, K₂O is greater than Na₂O. In some embodiments, total alkali oxides (R₂O) are less than about 7 mol % or less than about 6 mol % with K₂O>Na₂O.

In some embodiments, the glass compositions described herein can have one or more or all of the following compositional characteristics: (i) an As₂O₃ concentration of at most 0.05 to 1.0 mol %; (ii) an Sb₂O₃ concentration of at most 0.05 to 1.0 mol %; (iii) a SnO₂ concentration of at most 0.25 to 3.0 mol %.

As₂O₃ is an effective high temperature fining agent for display glasses, and in some embodiments described herein, As₂O₃ is used for fining because of its superior fining properties. However, As₂O₃ is poisonous and requires special handling during the glass manufacturing process. Accordingly, in certain embodiments, fining is performed without the use of substantial amounts of As₂O₃, i.e., the finished glass has at most 0.05 mole percent As₂O₃. In one embodiment, no As₂O₃ is purposely used in the fining of the glass. In such cases, the finished glass will typically have at most 0.005 mole percent As₂O₃ as a result of contaminants present in the batch materials and/or the equipment used to melt the batch materials.

Although not as toxic as As₂O₃, Sb₂O₃ is also poisonous and requires special handling. In addition, Sb₂O₃ raises the density, raises the CTE, and lowers the annealing point in comparison to glasses that use As₂O₃ or SnO₂ as a fining agent. Accordingly, in certain embodiments, fining is performed without the use of substantial amounts of Sb₂O₃, i.e., the finished glass has at most 0.05 mole percent Sb₂O₃. In another embodiment, no Sb₂O₃ is purposely used in the fining of the glass. In such cases, the finished glass will typically have at most 0.005 mole percent Sb₂O₃ as a result of contaminants present in the batch materials and/or the equipment used to melt the batch materials.

Compared to As₂O₃ and Sb₂O₃ fining, tin fining (i.e., SnO₂ fining) is less effective, but SnO₂ is a ubiquitous material that has no known hazardous properties. Also, for many years, SnO₂ has been a component of display glasses through the use of tin oxide electrodes in the Joule melting of the batch materials for such glasses. The presence of SnO₂ in display glasses has not resulted in any known adverse effects in the use of these glasses in the manufacture of liquid crystal displays. However, high concentrations of SnO₂ are not preferred as this can result in the formation of crystalline defects in display glasses. In one embodiment, the concentration of SnO₂ in the finished glass is less than or equal to 0.25 mole percent, in the range of about 0.07 to about 0.11 mol %, in the range of about 0 to about 2 mol %, from about 0 to about 3 mol %, and all subranges therebetween.

Tin fining can be used alone or in combination with other fining techniques if desired. For example, tin fining can be combined with halide fining, e.g., bromine fining. Other possible combinations include, but are not limited to, tin fining plus sulfate, sulfide, cerium oxide, mechanical bubbling, and/or vacuum fining. It is contemplated that these other fining techniques can be used alone. In certain embodiments, maintaining the (MgO+CaO+SrO+BaO)/Al₂O₃ ratio and individual alkaline earth concentrations within the ranges discussed above makes the fining process easier to perform and more effective.

In various embodiments, the glass may comprise R_(x)O where R is Li, Na, K, Rb, Cs, and x is 2, or R is Zn, Mg, Ca, Sr or Ba, and x is 1. In some embodiments, R_(x)O—Al₂O₃>0. In other embodiments, 0<R_(x)O—Al₂O₃<15, in some exemplary embodiments 10<R_(x)O—Al₂O₃<15. In some embodiments, R_(x)O/Al₂O₃ is between 0 and 10, between 0 and 5, greater than 1, or between 3.5 and 4.5, or between 2 and 6, or between 3 and 5, and all subranges therebetween. In further embodiments, Al₂O₃—R₂O<5, <0, between −3 and 2, or between −2 and 0.5, and all subranges therebetween. These ratios play significant roles in establishing the manufacturability of the glass article as well as determining its transmission performance.

In one or more embodiments and as noted above, exemplary glasses can have low concentrations of elements that produce visible absorption when in a glass matrix. Such absorbers include transition elements such as Ti, V, Cr, Mn, Fe, Co, Ni and Cu, and rare earth elements with partially-filled f-orbitals, including Ce, Pr, Nd, Sm, Eu, Tb, Dy, Ho, Er and Tm. Of these, the most abundant in conventional raw materials used for glass melting are Fe, Cr and Ni. Iron is a common contaminant in sand, the source of SiO₂, and is a typical contaminant as well in raw material sources for aluminum, magnesium and calcium. Chromium and nickel are typically present at low concentration in normal glass raw materials, but can be present in various ores of sand and must be controlled at a low concentration. Additionally, chromium and nickel can be introduced via contact with stainless steel, e.g., when raw material or cullet is jaw-crushed, through erosion of steel-lined mixers or screw feeders, or unintended contact with structural steel in the melting unit itself. The concentration of iron in some embodiments can be specifically less than 50 ppm, more specifically less than 40 ppm, or less than 25 ppm, and the concentration of Ni and Cr can be specifically less than 5 ppm, and more specifically less than 2 ppm. In further embodiments, the concentration of all other absorbers listed above may be less than 1 ppm for each. In various embodiments the glass comprises 1 ppm or less of Co, Ni, and Cr, or alternatively less than 1 ppm of Co, Ni, and Cr. In various embodiments, the transition elements (V, Cr, Mn, Fe, Co, Ni and Cu) may be present in the glass at 0.1 wt % or less. In some embodiments, the concentration of Fe, Cr, and/or Ni can be <about 50 ppm, <about 40 ppm, <about 30 ppm, <about 20 ppm, or <about 10 ppm.

In other embodiments, it has been discovered that the addition of certain transition metal oxides that do not cause absorption from 300 nm to 650 nm and that have absorption bands<about 300 nm will prevent network defects from forming processes and will prevent color centers (e.g., absorption of light from 300 nm to 650 nm) post UV exposure when curing ink since the bond by the transition metal oxide in the glass network will absorb the light instead of allowing the light to break up the fundamental bonds of the glass network. Thus, exemplary embodiments can include any one or combination of the following transition metal oxides to minimize UV color center formation: from about 0.1 mol % to about 4.0 mol % zinc oxide; from about 0.1 mol % to about 1.0 mol % titanium oxide; from about 0.1 mol % to about 1.0 mol % vanadium oxide; from about 0.1 mol % to about 1.0 mol % niobium oxide; from about 0.1 mol % to about 1.0 mol % manganese oxide; from about 0.1 mol % to about 2.0 mol % zirconium oxide; from about 0.1 mol % to about 1.0 mol % arsenic oxide; from about 0.1 mol % to about 1.0 mol % tin oxide; from about 0.1 mol % to about 1.0 mol % molybdenum oxide; from about 0.1 mol % to about 1.0 mol % antimony oxide; from about 0.1 mol % to about 1.0 mol % cerium oxide; and all subranges therebetween of any of the above listed transition metal oxides. In some embodiments, an exemplary glass can contain from 0.1 mol % to less than or no more than about 4.0 mol % of any combination of zinc oxide, titanium oxide, vanadium oxide, niobium oxide, manganese oxide, zirconium oxide, arsenic oxide, tin oxide, molybdenum oxide, antimony oxide, and cerium oxide.

The valence and coordination state of iron in a glass matrix can also be affected by the bulk composition of the glass. For example, iron redox ratio has been examined in molten glasses in the system SiO₂—K₂O—Al₂O₃ equilibrated in air at high temperature. It was found that the fraction of iron as Fe³⁺ increases with the ratio K₂O/K₂O+Al₂O₃), which in practical terms will translate to greater absorption at short wavelengths. In exploring this matrix effect, it was discovered that the ratios (Li₂O+Na₂O+K₂O+Rb₂O+Cs₂O)/Al₂O₃ and (MgO+CaO+ZnO+SrO+BaO)/Al₂O₃ can also be important for maximizing transmission in borosilicate glasses. Thus, for the R_(x)O ranges described above, transmission at exemplary wavelengths can be maximized for a given iron content. This is due in part to the higher proportion of Fe²⁺, and partially to matrix effects associated with the coordination environment of iron.

Glass Roughness

FIG. 3 is a graph showing the estimated light leakage in dB/m versus RMS roughness of an LGP. With reference to FIG. 3, it can be shown that surface scattering plays a role in LGPs as light is bouncing many times on the surfaces thereof. The curve depicted in FIG. 3 illustrates light leakage in dB/m as a function of the RMS roughness of the LGP. FIG. 3 shows that, to get below 1 dB/m, the surface quality needs to be better than about 0.6 nm RMS. This level of roughness can be achieved by either using fusion draw process or float glass followed by polishing. Such a model assumes that roughness acts like a Lambertian scattering surface which means that we are only considering high spatial frequency roughness. Therefore, roughness should be calculated by considering the power spectral density and only take into account frequencies that are higher than about 20 microns⁻¹. Surface roughness may be measured by atomic force microscopy (AFM); white light interferometry with a commercial system such as those manufactured by Zygo; or by laser confocal microscopy with a commercial system such as those provided by Keyence. The scattering from the surface may be measured by preparing a range of samples identical except for the surface roughness, and then measuring the internal transmittance of each as described below. The difference in internal transmission between samples is attributable to the scattering loss induced by the roughened surface.

UV Processing

In processing exemplary glass, ultraviolet (UV) light can also be used. For instance, light extraction features are often made by white printing dots on glass and UV is used to dry the ink. Also, extraction features can be made of a polymer layer with some specific structure on it and requires UV exposure for polymerization. It has been discovered that UV exposure of glass can significantly affect transmission. According to one or more embodiments, a filter can be used during glass processing of the glass for an LGP to eliminate all wavelengths below about 400 nm. One possible filter consists in using the same glass as the one that is currently exposed.

Glass Waviness

Glass waviness is somewhat different from roughness in the sense that it is much lower frequency (in the mm or larger range). As such, waviness does not contribute to extracting light since angles are very small but it modifies the efficiency of the extraction features since the efficiency is a function of the light guide thickness. Light extraction efficiency is, in general, inversely proportional to the waveguide thickness. Therefore, to keep high frequency image brightness fluctuations below 5% (which is the human perception threshold that resulted from our sparkle human perception analysis), the thickness of the glass needs to be constant within less than 5%. Exemplary embodiments can have an A-side waviness of less than 0.3 um, less than 0.2 um, less than 1 um, less than 0.08 um, or less than 0.06 um.

FIG. 4 is a graph showing an expected coupling (without Fresnel losses) as a function of distance between the LGP and LED for a 2 mm thick LED's coupled into a 2 mm thick LGP. With reference to FIG. 4, light injection in an exemplary embodiment usually involves placing the LGP in direct proximity to one or more light emitting diodes (LEDs). According to one or more embodiments, efficient coupling of light from an LED to the LGP involves using LED with a thickness or height that is less than or equal to the thickness of the glass. Thus, according to one or more embodiments, the distance from the LED to the LGP can be controlled to improve LED light injection. FIG. 4 shows the expected coupling (without Fresnel losses) as a function of that distance and considering 2 mm height LED's coupled into a 2 mm thick LGP. According to FIG. 4, the distance should be <about 0.5 mm to keep coupling>about 80%. When plastic such as PMMA is used as a conventional LGP material, putting the LGP in physical contact with the LED's is somewhat problematic. First, a minimum distance is needed to let the material expand. Also LEDs tend to heat up significantly and, in case of physical contact, PMMA can get close to its Tg (105° C. for PMMA). The temperature elevation that was measured when putting PMMA in contact with LED's was about 50° C. close by the LEDs. Thus for PMMA LGP, a minimum air gap is needed which degrades the coupling as shown in FIG. 4. According to embodiments of the subject matter in which glass LGPs are utilized, heating the glass is not a problem since Tg of glass is much higher and physical contact may actually be an advantage since glass has a thermal conduction coefficient that is large enough to make the LGP to be one additional heat dissipation mechanism.

FIG. 5 is a pictorial illustration of a coupling mechanism from an LED to a glass LGP. With reference to FIG. 5, assuming that the LED is close to a lambertian emitter and assuming the glass index of refraction is about 1.5, the angle α will stay smaller than 41.8 degrees (as in (1/1.5)) and the angle β will stay larger than 48.2 degrees (90−α). Since total internal reflection (TIR) angle is about 41.8 degrees, this means that all the light remains internal to the guide and coupling is close to 100%. At the level of the LED injection, the injection face may cause some diffusion which will increase the angle at which light is propagating into the LGP. In the event this angle becomes larger than the TIR angle, light may leak out of the LGP resulting in coupling losses. However, the condition for not introducing significant losses is that the angle in which light gets scattered should be less than 48.2−41.8=+/−6.4 degrees (scattering angle<12.8 degrees). Thus, according to one or more embodiments, a plurality of the edges of the LGP may have a mirror polish to improve LED coupling and TIR. In some embodiments, three of the four edges have a mirror polish. Of course, these angles are exemplary only and should not limit the scope of the claims appended herewith as exemplary scattering angles can be <20 degrees, <19 degrees, <18 degrees, <17 degrees, <16 degrees, <14 degrees, <13 degrees, <12 degrees, <11 degrees, or <10 degrees. Further, exemplary diffusion angles in reflection can be, but are not limited to, <15 degrees, <14 degrees, <13 degrees, <12 degrees, <11 degrees, <10 degrees, <9 degrees, <8 degrees, <7 degrees, <6 degrees, <5 degrees, <4 degrees, or <3 degrees.

FIG. 6 is a graph showing an expected angular energy distribution calculated from surface topology. With reference to FIG. 6, the typical texture of a grinded only edge is illustrated where roughness amplitude is relatively high (on the order of 1 nm) but special frequencies are relatively low (on the order of 20 microns) resulting in a low scattering angle. Further, this figure illustrates the expected angular energy distribution calculated from the surface topology. As can be seen, scattering angle can be much less than 12.8 degrees full width half maximum (FWHM).

In terms of surface definition, a surface can be characterized by a local slope distribution θ (x,y) that can be calculated, for instance, by taking the derivative of the surface profile. The angular deflection in the glass can be calculated, in first approximation as: θ′(x,y)=θ(x,y)/n Therefore, the condition on the surface roughness is θ (x,y)<n*6.4 degrees with TIR at the 2 adjacent edges.

FIG. 7 is a pictorial illustration showing total internal reflection of light at two adjacent edges of a glass LGP. With reference to FIG. 7, light injected into a first edge 130 can be incident on a second edge 140 adjacent to the injection edge and a third edge 150 adjacent to the injection edge, where the second edge 140 is opposite the third edge 150. The second and third edges may also have a low roughness so that the incident light undergoes total internal reflectance (TIR) from the two edges adjacent the first edge. In the event light is diffused or partially diffused at those interfaces, light may leak from each of those edges, thereby making the edges of an image appear darker. In some embodiments, light may be injected into the first edge 130 from an array of LED's 200 positioned along the first edge 130. The LED's may be located a distance of less than 0.5 mm from the light injection edge. According to one or more embodiments, the LED's may have a thickness or height that is less than or equal to the thickness of the glass sheet to provide efficient light coupling to the light guide plate 100. As discussed with reference to FIG. 1, FIG. 7 shows a single edge 130 injected with light, but the claimed subject matter should not be so limited as any one or several of the edges of an exemplary embodiment 100 can be injected with light. For example, in some embodiments, the first edge 130 and its opposing edge can both be injected with light. Additional embodiments may inject light at the second edge 140 and its opposing edge 150 rather than the first edge 130 and/or its opposing edge. According to one or more embodiments, the two edges 140, 150 may have a diffusion angle in reflection that is below 6.4 degrees such that the condition on the roughness shape is represented by θ (x,y)<6.4/2=3.2 degrees.

LCD Panel Rigidity

One attribute of LCD panels is the overall thickness. In conventional attempts to make thinner structures, lack of sufficient stiffness has become a serious problem. Stiffness, however, can be increased with an exemplary glass LGP since the elastic modulus of glass is considerably larger than that of PMMA. In some embodiments, to obtain a maximum benefit from a stiffness point of view, all elements of the panel can be bonded together at the edge.

FIG. 8 is a cross sectional illustration of an exemplary LCD panel with a LGP in accordance with one or more embodiments. With reference to FIG. 8, an exemplary embodiment of a panel structure 500 is provided. The structure comprises an LGP 100 mounted on a back plate 550 through which light can travel and be redirected toward the LCD or an observer. A structural element 555 may affix the LGP 100 to the back plate 550, and create a gap between the back face of the LGP and a face of the back plate. A reflective and/or diffusing film 540 may be positioned between the back face of the LGP 100 and the back plate 550 to send recycled light back through the LGP 100. A plurality of LEDs, organic light emitting diodes (OLEDs), or cold cathode fluorescent lamps (CCFLs) may be positioned adjacent to the light injection edge 130 of the LGP, where the LEDs have the same width as the thickness of the LGP 100, and are at the same height as the LGP 100. In other embodiments, the LEDs have a greater width and/or height as the thickness of the LGP 100. Conventional LCDs may employ LEDs or CCFLs packaged with color converting phosphors to produce white light. One or more backlight film(s) 570 may be positioned adjacent the front face of the LGP 100. An LCD panel 580 may also be positioned above the front face of the LGP 100 with a structural element 585, and the backlight film(s) 570 may be located in the gap between the LGP 100 and LCD panel 580. Light from the LGP 100 can then pass through the film 570, which can backscatter high angle light and reflect low angle light back toward the reflector film 540 for recycling and may serve to concentrate light in the forward direction (e.g., toward the user). A bezel 520 or other structural member may hold the layers of the assembly in place. A liquid crystal layer (not shown) may be used and may comprise an electro-optic material, the structure of which rotates upon application of an electric field, causing a polarization rotation of any light passing through it. Other optical components can include, e.g., prism films, polarizers, or TFT arrays, to name a few. According to various embodiments, the angular light filters disclosed herein can be paired with a transparent light guide plate in a transparent display device. In some embodiments, the LGP can be bonded to the structure (using optically clear adhesive OCA or pressure sensitive adhesive PSA) where the LGP is placed in optical contact with some of the structural elements of the panel. In other words, some of the light may leak out of the light guide through the adhesive. This leaked light can become scattered or absorbed by those structural elements. As explained above, the first edge where the LEDs are coupled into the LGP and the two adjacent edges where the light needs to be reflected in TIR can avoid this problem if properly prepared.

Exemplary widths and heights of the LGP generally depend upon the size of the respective LCD panel. It should be noted that embodiments of the present subject matter are applicable to any size LCD panel whether small (<40″ diagonal) or large (>40″ diagonal) displays. Exemplary dimensions for LGPs include, but are not limited to, 20″, 30″, 40″, 50″, 60″ diagonal or more.

FIG. 9 is a cross sectional illustration of an exemplary LCD panel with a LGP according to another embodiment. With reference to FIG. 9, additional embodiments can utilize a reflective layer. Losses in some embodiments can be minimized by inserting a reflective surface between the LGP and the epoxy by either metalizing the glass with, for instance, silver or inkjet print with reflective ink. In other embodiments, highly reflective films (such as Enhanced Specular Reflector films (made by 3M)) may be laminated with the LGP.

FIG. 10 is a pictorial illustration showing an LGP with adhesion pads according to additional embodiments. With reference to FIG. 10, adhesion pads instead of a continuous adhesive can be used in which the pads 600 are shown as a series of dark squares. Thus, to limit the surface of LGP that is optically connected to the structural elements, the illustrated embodiment can employ 5×5 mm square pads every 50 mm to provide sufficient adhesion where extracted light is less than 4%. Of course, the pads 600 may be circular or another polygon in form and may be provided in any array or spacing and such a description should not limit the scope of the claims appended herewith.

Color Shift Compensation

In prior glasses although decreasing iron concentration minimized absorption and yellow shift, it was difficult to eliminate it completely. The Δx, Δy in the measured for PMMA for a propagation distance of about 700 mm was 0.0021 and 0.0063. In exemplary glasses having the compositional ranges described herein, the color shift Δy was <0.015 and in exemplary embodiments was less than 0.0021, and less than 0.0063. For example, in some embodiments, the color shift was measured as 0.007842 and in other embodiments was measured as 0.005827. In other embodiments, an exemplary glass sheet can comprise a color shift Δy less than 0.015, such as ranging from about 0.001 to about 0.015 (e.g., about 0.001, 0.002, 0.003, 0.004, 0.005, 0.006, 0.007, 0.008, 0.009, 0.010, 0.011, 0.012, 0.013, 0.014, or 0.015). In other embodiments, the transparent substrate can comprise a color shift less than 0.008, less than about 0.005, or less than about 0.003. Color shift may be characterized by measuring variation in the x and/or y chromaticity coordinates along a length L using the CIE 1931 standard for color measurements for a given source illumination. For exemplary glass light-guide plates the color shift Δy can be reported as Δy=y(L₂)−y(L₁) where L₂ and L₁ are Z positions along the panel or substrate direction away from the source launch (e.g., LED or otherwise) and where L₂−L₁=0.5 meters. Exemplary light-guide plates described herein have Δy<0.015, Δy<0.005, Δy<0.003, or Δy<0.001. The color shift of a light guide plate can be estimated by measuring the optical absorption of the light guide plate, using the optical absorption to calculate the internal transmission of the LGP over 0.5 m, and then multiplying the resulting transmission curve by a typical LED source used in LCD backlights such as the Nichia NFSW157D-E. One can then use the CIE color matching functions to compute the (X, Y, Z) tristimulus values of this spectrum. These values are then normalized by their sum to provide the (x,y) chromaticity coordinates. The difference between the (x,y) values of the LED spectrum multiplied by the 0.5 m LGP transmission and the (x,y) values of the original LED spectrum is the estimate of the color shift contribution of the light guide material. To address residual color shift, several exemplary solutions may be implemented. In one embodiment, light guide blue painting can be employed. By blue painting the light guide, one can artificially increase absorption in red and green and increase light extraction in blue. Accordingly, knowing how much differential color absorption exists, a blue paint pattern can be back calculated and applied that can compensate for color shift. In one or more embodiments, shallow surface scattering features can be employed to extract light with an efficiency that depends on the wavelength. As an example, a square grating has a maximum of efficiency when the optical path difference equals half of the wavelength. Accordingly, exemplary textures can be used to preferentially extract blue and can be added to the main light extraction texture. In additional embodiments, image processing can also be utilized. For example, an image filter can be applied that will attenuate blue close to the edge where light gets injected. This may require shifting the color of the LEDs themselves to keep the right white color. In further embodiments, pixel geometry can be used to address color shift by adjusting the surface ratio of the RGB pixels in the panel and increasing the surface of the blue pixels far away from the edge where the light gets injected.

Examples and Glass Compositions

Exemplary compositions as heretofore described can thus be used to achieve a strain point ranging from about 600° C. to about 700° C., from about 600° C. to about 670° C. and all subranges therebetween. In one embodiment, the strain point is about 547° C., and in another embodiment, the strain point is about 565° C. An exemplary annealing point can range from about 650° C. to about 725° C. and all subranges therebetween. An exemplary softening point of a glass ranges from about 880° C. to about 960° C., and all subranges therebetween. The density of exemplary glass compositions can range from about 2.5 gm/cc @ 20 C to about 2.7 gm/cc @ 20 C, from about 2.513 gm/cc @ 20 C to about 2.7 gm/cc @ 20 C, or from about 2.5 gm/cc @ 20 C to about 2.613 gm/cc @ 20 C and all subranges therebetween. CTEs (0-300° C.) for exemplary embodiments can range from about 30×10−7/° C. to about 95×10−7/° C., from about 55×10−7/° C. to about 64×10−7/° C., or from about 55×10−7/° C. to about 80×10−7/° C. and all subranges therebetween. In one embodiment the CTE is about 55.7×10−7/° C. and in another embodiment the CTE is about 69×10−7/° C.

Certain embodiments and compositions described herein have provided an internal transmission from 400-700 nm greater than 90%, greater than 91%, greater than 92%, greater than 93%, greater than 94%, and even greater than 95%. Internal transmittance can be measured by comparing the light transmitted through a sample to the light emitted from a source. Broadband, incoherent light may be cylindrically focused on the end of the material to be tested. The light emitted from the far side may be collected by an integrating sphere fiber coupled to a spectrometer and forms the sample data. Reference data is obtained by removing the material under test from the system, translating the integrating sphere directly in front of the focusing optic, and collecting the light through the same apparatus as the reference data. The absorption at a given wavelength is then given by:

${{adsorption}\left( {{dB}\text{/}m} \right)} = \frac{{- 10}\log\frac{T_{{sample}\mspace{14mu}{data}}}{T_{{reference}\mspace{14mu}{data}}}}{\left( {{Pathlength}_{\;{{sample}\mspace{14mu}{data}}} - {Pathlength}_{\;{{reference}\mspace{14mu}{data}}}} \right)}$ The internal transmittance over 0.5 m is given by: Transmittance(%)=100×10^(−absorption×0.5/10) Thus, exemplary embodiments described herein can have an internal transmittance at 450 nm with 500 mm in length of greater than 85%, greater than 90%, greater than 91%, greater than 92%, greater than 93%, greater than 94%, and even greater than 95%. Exemplary embodiments described herein can also have an internal transmittance at 550 nm with 500 mm in length of greater than 90%, greater than 91%, greater than 92%, greater than 93%, greater than 94%, and even greater than 96%. Further embodiments described herein can have a transmittance at 630 nm with 500 mm in length of greater than 85%, greater than 90%, greater than 91%, greater than 92%, greater than 93%, greater than 94%, and even greater than 95%.

In one or more embodiments, the LGP has a width of at least about 1270 mm and a thickness of between about 0.5 mm and about 3.0 mm, wherein the transmittance of the LGP is at least 80% per 500 mm. In various embodiments, the thickness of the LGP is between about 1 mm and about 8 mm, and the width of the plate is between about 1100 mm and about 1300 mm.

In one or more embodiments, the LGP can be strengthened. For example, certain characteristics, such as a moderate compressive stress (CS), high depth of compressive layer (DOL), and/or moderate central tension (CT) can be provided in an exemplary glass sheet used for a LGP. One exemplary process includes chemically strengthening the glass by preparing a glass sheet capable of ion exchange. The glass sheet can then be subjected to an ion exchange process, and thereafter the glass sheet can be subjected to an anneal process if necessary. Of course, if the CS and DOL of the glass sheet are desired at the levels resulting from the ion exchange step, then no annealing step is required. In other embodiments, an acid etching process can be used to increase the CS on appropriate glass surfaces. The ion exchange process can involve subjecting the glass sheet to a molten salt bath including KNO₃, preferably relatively pure KNO₃ for one or more first temperatures within the range of about 400-500° C. and/or for a first time period within the range of about 1-24 hours, such as, but not limited to, about 8 hours. It is noted that other salt bath compositions are possible and would be within the skill level of an artisan to consider such alternatives. Thus, the disclosure of KNO₃ should not limit the scope of the claims appended herewith. Such an exemplary ion exchange process can produce an initial CS at the surface of the glass sheet, an initial DOL into the glass sheet, and an initial CT within the glass sheet. Annealing can then produce a final CS, final DOL and final CT as desired.

Examples

The following examples are set forth below to illustrate the methods and results according to the disclosed subject matter. These examples are not intended to be inclusive of all embodiments of the subject matter disclosed herein, but rather to illustrate representative methods and results. These examples are not intended to exclude equivalents and variations of the present disclosure which are apparent to one skilled in the art.

Efforts have been made to ensure accuracy with respect to numbers (e.g., amounts, temperature, etc.) but some errors and deviations should be accounted for. Unless indicated otherwise, temperature is in ° C. or is at ambient temperature, and pressure is at or near atmospheric. The compositions themselves are given in mole percent on an oxide basis and have been normalized to 100%. There are numerous variations and combinations of reaction conditions, e.g., component concentrations, temperatures, pressures and other reaction ranges and conditions that can be used to optimize the product purity and yield obtained from the described process. Only reasonable and routine experimentation will be required to optimize such process conditions.

The glass properties set forth herein and in the tables below were determined in accordance with techniques conventional in the glass art. Thus, the linear coefficient of thermal expansion (CTE) over the temperature range 25-300° C. is expressed in terms of ×10-7/° C. and the annealing point is expressed in terms of ° C. These can be determined from fiber elongation techniques (ASTM references E228-85 and C336, respectively). The density in terms of grams/cm3 was measured via the Archimedes method (ASTM C693). The melting temperature in terms of ° C. (defined as the temperature at which the glass melt demonstrates a viscosity of 200 poises) was calculated employing a Fulcher equation fit to high temperature viscosity data measured via rotating cylinders viscometry (ASTM C965-81), and including a low temperature viscosity point at 10^(13.18) P measured by beam bending technique to improve the Fulcher equation fit for the full range of temperatures from annealing point up to melting temperatures.

The liquidus temperature of the glass in terms of ° C. was measured using the standard gradient boat liquidus method of ASTM C829-81. This involves placing crushed glass particles in a platinum boat, placing the boat in a furnace having a region of gradient temperatures, heating the boat in an appropriate temperature region for 24 hours, and determining by means of microscopic examination the highest temperature at which crystals appear in the interior of the glass. More particularly, the glass sample is removed from the Pt boat in one piece, and examined using polarized light microscopy to identify the location and nature of crystals which have formed against the Pt and air interfaces, and in the interior of the sample. Because the gradient of the furnace is very well known, temperature vs. location can be well estimated, within 5-10° C. The temperature at which crystals are observed in the internal portion of the sample is taken to represent the liquidus of the glass (for the corresponding test period). Testing is sometimes carried out at longer times (e.g. 72 hours), to observe slower growing phases. The liquidus viscosity in poises was determined from the liquidus temperature and the coefficients of the Fulcher equation.

The exemplary glasses of the tables herein were prepared using a commercial sand as a silica source, milled such that 90% by weight passed through a standard. U.S. 100 mesh sieve. Alumina was the alumina source, periclase was the source for MgO, limestone the source for CaO, strontium carbonate, strontium nitrate or a mix thereof was the source for SrO, barium carbonate was the source for BaO, and tin (IV) oxide was the source for SnO2. The raw materials were thoroughly mixed, loaded into a platinum vessel suspended in a gas-oxy furnace, melted first at 1550 C for 4 hours where after the melt was quenched into water. Glass grains retrieved are dried and reloaded into the Pt crucible for a second round of melting. Second inciting is made over night at 1550 to 1650 C temperature. Double melting of the glass ensures homogeneity. Glasses are poured onto a stainless steel table to form patties of about 1 cm thickness. The resulting patties of glass were annealed at or near the annealing point, and then subjected to various experimental methods to determine physical, viscous and liquidus attributes.

These methods are not unique, and the glasses of the tables herein can be prepared using standard methods well-known to those skilled in the art. Such methods include a continuous melting process, such as would be performed in a continuous melting process, wherein the inciter used in the continuous melting process is heated by gas, by electric power, or combinations thereof.

Raw materials appropriate for producing exemplary glasses include commercially available sands as sources for SiO2; alumina, aluminum hydroxide, hydrated forms of alumina, and various aluminosilicates, nitrates and halides as sources for Al2O3: boric acid, anhydrous boric acid and boric oxide as sources for B2O3; periclase, dolomite (also a source of CaO), magnesia, magnesium carbonate, magnesium hydroxide, and various forms of magnesium silicates, aluminosilicates, nitrates and halides as sources for MgO; limestone, aragonite, dolomite (also a source of MgO), wolastonite, and various forms of calcium silicates, aluminosilicates, nitrates and halides as sources for CaO; and oxides, carbonates, nitrates and halides of strontium and barium. If a chemical fining agent is desired, tin can be added as SnO2, as a mixed oxide with another major glass component (e.g., CaSnO3), or in oxidizing conditions as SnO, tin oxalate, tin halide, or other compounds of tin known to those skilled in the art.

The glasses in the tables herein can contain SnO2 as a fining agent, but other chemical fining agents could also be employed to obtain glass of sufficient quality for display applications. For example, exemplary glasses could employ any one or combinations of As2O3, Sb2O3, CeO2, Fe2O3, and halides as deliberate additions to facilitate fining, and any of these could be used in conjunction with the SnO2 chemical fining agent shown in the examples. Of these, As2O3 and Sb2O3 are generally recognized as hazardous materials, subject to control in waste streams such as might be generated in the course of glass manufacture or in the processing of TFT panels. It is therefore desirable to limit the concentration of As2O3 and Sb2O3 individually or in combination to no more than 0.005 mol %.

In addition to the elements deliberately incorporated into exemplary glasses, nearly all stable elements in the periodic table are present in glasses at some level, either through low levels of contamination in the raw materials, through high-temperature erosion of refractories and precious metals in the manufacturing process, or through deliberate introduction at low levels to fine tune the attributes of the final glass. For example, zirconium may be introduced as a contaminant via interaction with zirconium-rich refractories. As a further example, platinum and rhodium may be introduced via interactions with precious metals. As a further example, iron may be introduced as a tramp in raw materials, or deliberately added to enhance control of gaseous inclusions. As a further example, manganese may be introduced to control color or to enhance control of gaseous inclusions.

Hydrogen is inevitably present in the form of the hydroxyl anion, OH—, and its presence can be ascertained via standard infrared spectroscopy techniques. Dissolved hydroxyl ions significantly and nonlinearly impact the annealing point of exemplary glasses, and thus to obtain the desired annealing point it may be necessary to adjust the concentrations of major oxide components so as to compensate. Hydroxyl ion concentration can be controlled to some extent through choice of raw materials or choice of melting system. For example, boric acid is a major source of hydroxyls, and replacing boric acid with boric oxide can be a useful means to control hydroxyl concentration in the final glass. The same reasoning applies to other potential raw materials comprising hydroxyl ions, hydrates, or compounds comprising physisorbed or chemisorbed water molecules. If burners are used in the melting process, then hydroxyl ions can also be introduced through the combustion products from combustion of natural gas and related hydrocarbons, and thus it may be desirable to shift the energy used in melting from burners to electrodes to compensate. Alternatively, one might instead employ an iterative process of adjusting major oxide components so as to compensate for the deleterious impact of dissolved hydroxyl ions.

Sulfur is often present in natural gas, and likewise is a tramp component in many carbonate, nitrate, halide, and oxide raw materials. In the form of SO2, sulfur can be a troublesome source of gaseous inclusions. The tendency to form SO2-rich defects can be managed to a significant degree by controlling sulfur levels in the raw materials, and by incorporating low levels of comparatively reduced multivalent cations into the glass matrix. While not wishing to be bound by theory, it appears that SO2-rich gaseous inclusions arise primarily through reduction of sulfate (SO4=) dissolved in the glass. The elevated barium concentrations of exemplary glasses appear to increase sulfur retention in the glass in early stages of melting, but as noted above, barium is required to obtain low liquidus temperature, and hence high T35k-Tliq and high liquidus viscosity. Deliberately controlling sulfur levels in raw materials to a low level is a useful means of reducing dissolved sulfur (presumably as sulfate) in the glass. In particular, sulfur is preferably less than 200 ppm by weight in the batch materials, and more preferably less than 100 ppm by weight in the batch materials.

Reduced multivalents can also be used to control the tendency of exemplary glasses to form SO2 blisters. While not wishing to be bound to theory, these elements behave as potential electron donors that suppress the electromotive force for sulfate reduction, Sulfate reduction can be written in terms of a half reaction such as SO4=→SO2+O2+2e− where e− denotes an electron. The “equilibrium constant” for the half reaction is Keq=[SO2][O2][e−]2/[SO4=] where the brackets denote chemical activities. Ideally one would like to force the reaction so as to create sulfate from SO2, O2 and 2e−. Adding nitrates, peroxides, or other oxygen-rich raw materials may help, but also may work against sulfate reduction in the early stages of melting, which may counteract the benefits of adding them in the first place. SO2 has very low solubility in most glasses, and so is impractical to add to the glass melting process. Electrons may be “added” through reduced multivalents. For example, an appropriate electron-donating half reaction for ferrous iron (Fe2+) is expressed as 2Fe2+→2Fe3++2e−

This “activity” of electrons can force the sulfate reduction reaction to the left, stabilizing SO4=in the glass. Suitable reduced multivalents include, but are not limited to, Fe2+, Mn2+, Sn2+, Sb3+, As3+, V3+, Ti3+, and others familiar to those skilled in the art. In each case, it may be important to minimize the concentrations of such components so as to avoid deleterious impact on color of the glass, or in the case of As and Sb, to avoid adding such components at a high enough level so as to complication of waste management in an end-user's process.

In addition to the major oxides components of exemplary glasses, and the minor or tramp constituents noted above, halides may be present at various levels, either as contaminants introduced through the choice of raw materials, or as deliberate components used to eliminate gaseous inclusions in the glass. As a fining agent, halides may be incorporated at a level of about 0.4 mol % or less, though it is generally desirable to use lower amounts if possible to avoid corrosion of off-gas handling equipment. In some embodiments, the concentrations of individual halide elements are below about 200 ppm by weight for each individual halide, or below about 800 ppm by weight for the sum of all halide elements.

In addition to these major oxide components, minor and tramp components, multivalents and halide fining agents, it may be useful to incorporate low concentrations of other colorless oxide components to achieve desired physical, solarization, optical or viscoelastic properties. Such oxides include, but are not limited to, TiO2, ZrO2, HfO2, Nb2O5, Ta2O5, MoO3, WO3, ZnO, In2O3, Ga2O3, Bi2O3, GeO2, PbO, SeO3, TeO2, Y2O3, La2O3, Gd2O3, and others known to those skilled in the art. By adjusting the relative proportions of the major oxide components of exemplary glasses, such colorless oxides can be added to a level of up to about 2 mol % to 3 mol % without unacceptable impact to annealing point, T35k-Tliq or liquidus viscosity. For example, some embodiments can include any one or combination of the following transition metal oxides to minimize UV color center formation: from about 0.1 mol % to about 4.0 mol % zinc oxide; from about 0.1 mol % to about 1.0 mol % titanium oxide; from about 0.1 mol % to about 1.0 mol % vanadium oxide; from about 0.1 mol % to about 1.0 mol % niobium oxide; from about 0.1 mol % to about 1.0 mol % manganese oxide; from about 0.1 mol % to about 2.0 mol % zirconium oxide; from about 0.1 mol % to about 1.0 mol % arsenic oxide; from about 0.1 mol % to about 1.0 mol % tin oxide; from about 0.1 mol % to about 1.0 mol % molybdenum oxide; from about 0.1 mol % to about 1.0 mol % antimony oxide; from about 0.1 mol % to about 1.0 mol % cerium oxide; and all subranges therebetween of any of the above listed transition metal oxides. In some embodiments, an exemplary glass can contain from 0.1 mol % to less than or no more than about 4.0 mol % of any combination of zinc oxide, titanium oxide, vanadium oxide, niobium oxide, manganese oxide, zirconium oxide, arsenic oxide, tin oxide, molybdenum oxide, antimony oxide, and cerium oxide.

Some exemplary embodiments include a glass article or sheet comprising SiO₂ in the range of about 74 to 77 mol %, Al₂O₃ in the range of about 3 to 6 mol %, R₂O in the range of about 4 to 7 mol %, of which 0 to 2 mol % is Na₂O, B₂O₃ in the range of about 0 to 3.5 mol %, ZrO₂ in the range of about 0 to 1.7 mol %, RO in the range of about 11 to 16 mol %, and ZnO in the range of about 0 to 4 mol %.

During experimentation, some glasses were doped with iron at 0.025-0.05 mol % level to introduce enough absorption that optical transmission was possible to measure on lab scale. Absorption measurements were made on at least samples with different thicknesses to achieve the accuracy needed, and for the transmission values measured and discussed in further detail below, the measured absorption was normalized with the help of ICP measured iron content for a 50 cm path length in a glass with 14 ppm Fe. It was discovered that to achieve acceptable transmission values, the impurity level must be very low, on the order of <60 ppm total Fe, Cr and Ni. In some embodiments, the impurity levels should be Fe<20 ppm, Cr<5 ppm, and Ni<5 ppm.

During experimentation, a predominant portion of the changes in absorption (and thus transmission) were found to be related to the redox change in the glass. A redox change will change the Sn⁴⁺/Sn²⁺ ratio which further defines the redox state of other multivalent ions in the glass. The content of tin among all multivalents is the highest, thus it functions as the master and other redox ratios will be defined by tin. The impurity that most affects absorption in the visible wavelengths was found to be iron as Fe²⁺ has its absorption peak in the infrared wavelengths but the tail of it reaches to red and green wavelengths. Fe³⁺ has its absorption peaks in UV wavelengths, and it will affect the blue end of the visible spectrum; however, this is very small compared to the effect of Fe²⁺. Thus, in exemplary embodiments it is preferred to have a more oxidized glass melt.

The oxidation state of a glass melt is controlled by all the oxides in it, for example, alkali ions make the SnO₂ more stable than SnO, thus giving a more oxidized melt. Thus, by altering the composition the redox state of the iron in the glass can be affected, and the induced absorption by iron in visible wavelengths can be minimized. Of course, other oxides also induce absorption, and NiO and Cr₂O₃ are also of concern as they are present as impurities in raw materials. For example, NiO has an absorption band that can change considerably with compositions and ranges from 430 nm to 630 nm, and Cr₂O₃ has absorption peaks at 450 nm and 650 nm. FIG. 11 is a graph depicting transmission values of exemplary glass compositions doped individually with Fe₂O₃, NiO, and Cr₂O₃. With reference to FIG. 11, it can be observed that iron reduced blue and red transmission while nickel and chromium together have a large effect at 450 nm. The effect of NiO appears to be more pronounced in these RO modified glasses as compared to R₂O modified glasses, thus it is of great importance to reduce the amount of NiO in exemplary glasses.

In exemplary embodiments where SiO₂ is high, over 74 mol % and with a corresponding low Al₂O₃ and B₂O₃ mol %, the alkaline earth oxides become the main modifiers, and liquid-liquid phase separation is a concern. Smaller ROs tend to increase the propensity for phase separation. Thus, by utilizing a mixture of alkaline earth oxides phase separation can be suppressed in exemplary glasses. Through the utilization of alkali, e.g., K₂O, Li₂O, Na₂O, several positive effects can be observed (see Table 1 below and FIG. 12). FIG. 12 is a graph depicting transmission values of exemplary glass compositions with varied R₂O types, and Table 1 provides, for a fixed base glass, a variation of alkali modifiers. With reference to Table 1 and FIG. 12, such effects include a decrease in liquidus temperature, an increase in liquidus viscosity, and an improvement in transmission at all wavelengths due, in part, to the change in redox state of the glass that the identity of the alkali drives.

TABLE 1 T(η = T(η = Li₂O Na₂O K₂O T(liq) η(Liq) 200 P) 35 kP) Glass [mol %] [mol %] [mol %] [° C.] [P] [° C.] [° C.] A1 1.33 1.28 1.26 1250  7500 1625 1147 B1 2.93 0.98 1215  15000 1633 1161 C1 0.99 2.93 1110* 182200* 1647 1197 *24 h gradient boat measurement, while others are 72 h

In additional embodiments, the effect of alumina to alkali ratio was compared with a set of glasses (see Table 2 and FIG. 13) where variation was introduced only to the ratio of Al₂O₃/R₂O, and the remainder of the glass composition was batched exactly the same. FIG. 13 is a graph depicting transmission values for glasses in Table 2, and Table 2 provides Al₂O₃/R₂O variations from 0.79 to 1.28 in a base glass.

TABLE 2 Al₂O₃ Na₂O K₂O Al₂O₃/ T(liq) η(Liq) T(η = 200 P) T(η = 35 kP) Glass [mol %] [mol %] [mol %] R₂O [° C.] [P] [° C.] [° C.] C1 3.93 0.99 2.93 1.0 1110* 182200* 1647 1197 D1 4.45 0.98 2.45 1.30 1155  88600 1647 1207 E1 3.45 0.98 3.42 0.78 1110 119400 1626 1176 *24 h gradient boat measurement, while others are 72 h

With reference to FIG. 13 and Table 2, 8 mol % was used in total for Al₂O₃ and R₂O, of which 1 mol % was kept as Na₂O. It can be observed that transmission was highest in green and red wavelengths (550 nm and 630 nm) for Al₂O₃/R₂O=1, while at 450 nm (blue) the curves overlap (see FIG. 13). Liquidus viscosity was highest for Al₂O₃/R₂O=1, while still far away from 1 MP as needed. Though as it is measured only for 24 h as compared to 72 h used for the others, this gives an artificially lower liquidus temperature for this glass. Generally liquidus temperature will be 10-50° C. higher for a 72 h measurement compared to 24 h measurement. This would take the Al₂O₃/R₂O=1 glass close to the Al₂O₃/R₂O<1 glass.

In other embodiments, it was observed that the type of alkaline earth ion affects several properties of the glass. It is well known that large ROs (e.g., BaO) reduce liquidus temperature and reduce isoviscous temperatures. This was also observed for the base glass composition provided in Table 3 below. But it was discovered that the identity of the alkaline earth modifier also has a pronounced effect on the measured transmission of a glass article. FIG. 14 is a graph depicting transmission values for glasses having varied alkaline earths. With reference to FIG. 14, a reduction in red and green light transmission can be observed with an increasing RO size, which is indicative of a redox change of the iron. Some exemplary glasses with evenly distributed ROs (e.g., BaO, SrO, MgO, CaO) can be preferable. In some embodiments, utilizing a mixture of modifiers has the effect of reducing crystallization tendency, but as really the BaO has a larger suppression on liquidus it would be great to use but at same time it is provides poor red transmission. Thus, in the end using a mix of all gives a good compromise with not too much BaO to reduce transmission or provide high density and not too much MgO or CaO which can promote phase separation. Other exemplary glasses having BaO batched as SrO may also be preferable. One benefit of BaO can be observed when comparing the two last examples in Table 3, where H1 (having BaO) as compared to I1 (having SrO) has 100° C. lower liquidus temperature and thus a considerably higher liquidus viscosity.

TABLE 3 T(η = T(η = T(200 P − MgO CaO SrO BaO T(liq) η(Liq) 200 P) 35 kP) 35 kP) Glass [mol %] [mol %] [mol %] [mol %] [° C.] [P] [° C.] [° C.] [° C.] Fl 3.72 3.83 3.87 3.88 1110* 182200* 1647 1197 449 G1 5.3 9.7 1095*  80900* 1580 1140 440 H1 3.72 3.84 7.60 0.08 1160  74000 1658 1200 466 I1 3.66 3.83 0.15 7.67 1075 291800 1634 1185 450 *24 h gradient boat measurement, while others are 72 h.

As discussed above, having Al₂O₃═R₂O provided a low absorbance as well as a relatively high liquidus viscosity. As shown in Table 4 below and FIGS. 15A and 15B, it can be observed that increasing the total amount of Al₂O₃+R₂O at the cost of RO decreases liquidus temperature, increases liquidus viscosity, and maintains the isoviscosity temperatures of 200 P and 35 kP between 1700 and about 1200 C. It was also observed that in boron containing glasses, increasing Al₂O₃+R₂O introduces very little change to transmission of the glasses while in the boron free glasses an improvement at all wavelengths was observed (see FIGS. 15A and 15B). This phenomenon is related to both the increase in Al₂O₃ as well as to the decrease in the amount of large ROs.

TABLE 4 T(η = T(η = T(200 P − Al₂O₃ R₂O RO B₂O₃ T(liq) η(Liq) 200 P) 35 kP) 35 kP) Glass [mol %] [mol %] [mol %] [mol %] [° C.] [P] [° C.] [° C.] [° C.] J1 3.93 3.92 15.29 1.5 1110* 182200* 1647 1197 449 K1 4.92 4.73 13.35 1.49 1050* 690400* 1688 1206 482 L1 3.46 3.45 17.61 0 1180  42000 1621 1190 431 M1 3.94 3.95 16.70 0 1085 340000 1633 1198 435 N1 4.96 4.91 14.84 0 1070* 511900* 1677 1209 468 *24 h gradient boat measurement, while others are 72 h

In some embodiments, it was found that an addition of a moderate amount of ZrO₂ instead of SiO₂ decreased the 200 P temperature with little effect to liquidus temperature which has the combined effect of increasing liquidus viscosity (see Table 5). When too much ZrO₂ was added, however, it was found that the liquidus temperature increased dramatically (last example in Table 5). It was also observed that only the 200 P temperature decreased while the 35 kP temperature stayed constant when ZrO₂ is added, thus the T(200 P-35 kP) decreased which means that less heat is needed to be removed during forming which would allow for higher flow rates. Table 6 below also shows the difference when ZrO₂ is added either for SiO₂ or for RO. With the latter, modifiers were removed from the glass, increasing both 200 P and 35 kP temperatures while still reducing their difference and not affecting liquidus temperature thereby allowing for a very high liquidus viscosity. It was observed that transmission was little affected or not at all with ZrO₂ addition (the effect being the decrease in transmission at blue wavelengths (see FIGS. 16A and 16B).

TABLE 5 T(η = T(η = T(200 P − SiO₂ ZrO₂ Al₂O₃ R₂O RO T(liq) η(Liq) 200 P) 35 kP) 35 kP) Glass [mol %] [mol %] [mol %] [mol %] [mol %] [° C.] [P] [° C.] [° C.] [° C.] O1 75.36 0 4.92 4.73 13.35 1050* 690400* 1688 1206 482 P1 73.71 1.546 4.96 4.90 13.29 1050* 881500* 1664 1210 455 Q1 75.19 0 3.93 3.92 15.29 1110* 182200* 1647 1197 449 R1 73.83 1.46 3.95 3.92 15.21 1075 433600 1616 1197 421 S1 72.28 2.93 3.94 3.95 15.22 1250  14400 1607 1199 406 *24 h gradient boat measurement, while others are 72 h

TABLE 6 T(η = T(η = T(200 P − SiO₂ B₂O₃ ZrO₂ RO T(liq) η(Liq) 200 P) 35 kP) 35 kP) Glass [mol %] [mol %] [mol %] [mol %] [° C.] [P] [° C.] [° C.] [° C.] T1 75.36 1.49 0 13.35 1050*  690400* 1688 1206 482 U1 75.13 0 0 14.84 1070*  511900* 1677 1209 468 V1 73.71 1.51 1.46 13.29 1050*  881500* 1664 1210 455 W1 75.21 0 1.46 13.29 1075* 1034700* 1698 1243 455 *24 h gradient boat measurement, while others are 72 h

It was also discovered that if ZnO was added to a ZrO₂ containing glass instead of BaO, the liquidus phase changes to ZrSiO₄, and the liquidus temperature increases by 200-300° C. When BaO is replaced by ZnO in a glass without ZrO₂, the effects are generally negative, e.g., both 35 kP, 200 P and T(200 P-35 kP) increase as well as liquidus temperature, transmission in green and red improve, which is expected as the amount of the largest RO decreases.

It has been observed that generally the higher R₂O content glasses produce a greater amount of fusion line blistering and alkali-free glasses (e.g., tramp levels of R₂O) have little blistering. It was discovered that glasses having an R₂O/RO value greater than or equal to 1 provided a considerable amount of blistering when flooded onto a forming member (e.g., isopipe). Exemplary glasses, however, with an R₂O/RO ratio less than 1 have a positive impact on reducing the production of such blisters. In some embodiments the R₂O/RO ranges from 0.3 to less than 1.0. In other embodiments the R₂O/RO ranges from 0.38 to 0.53.

Combining the knowledge discussed above, exemplary compositions were developed that are highly transparent in the visible wavelengths and that have favorable viscosity for fusion forming. Generally one needs 35 kP temperature around 1200° C. or above, 200 P temperature below or around 1700° C., and T(200 P)-T(35 kP) as small as possible to allow for high flow rates. Exemplary glasses provided in Table 7 below contain a transmission>94% at 550 nm when measured over a 50 cm length, a transmission>92% at 450 nm when measured over a 50 cm length, and a transmission at 630 nm as high as possible, preferably over 86%. It was discovered that these attributes can be accomplished with glass compositions having SiO₂>70 mol %, >73 mol %, in a range between 70 to 80 mol %, in a range between 73 to 80 mol %, and in a range between 73 to 77 mol %. The glass compositions can have a lower Al₂O₃ mol %, such as in a range<8 mol %, <6 mol %, between 2 to 6 mol %, or between 4 to 6 mol %. Exemplary glass compositions also include a B₂O₃ constituent<6 mol %, between 0 to 6 mol %, between 0 to 3.5 mol %, or between 0 to 4 mol %.

Exemplary glass compositions can include, in some embodiments, alkali oxide modifiers such as Na₂O in a range of <5 mol %, <4 mol %, or between 0 to 3 mol %, K₂O in a range of <9 mol %, <8 mol %, between 0 to 9 mol %, between 0 to 8 mol %, between 2 to 7 mol %, or between 2.5 to 7 mol %, or Li₂O in a range of <2 mol %, <1.5 mol %, or between 0 and 1.5 mol %. In other embodiments total R₂O is in the range of about 4 to 7 mol %, of which 0 to 2 mol % is Na₂O. In exemplary embodiments, K₂O>Na₂O, and Al₂O₃−(Na₂O+K₂O)=−2 to 0.5.

Exemplary glass compositions can include, in some embodiments, alkaline earth modifiers such as MgO in the range of <6 mol %, <5 mol %, between 0 to 6 mol %, between 0 to 5 mol %, or between 2 to 4 mol %, CaO in the range of <6 mol %, <5 mol %, between 0 to 6 mol %, between 0 to 5 mol %, or between 2.4 to 4.5 mol %. Additional alkaline earth modifiers include SrO in the range of <6 mol %, <5 mol %, between 0 to 6 mol %, between 0 to 5 mol %, or between 2.5 to 5 mol %, BaO in the range of <6 mol %, <5 mol %, between 0 to 6 mol %, between 0 to 5 mol %, or between 1 to 4 mol %, and ZrO₂ in the range of <4 mol %, <3 mol %, between 0 to 4 mol %, between 0 to 3 mol %, or between 0 to 2 mol %. Total RO can be in the range of about 10 to 20 mol %, between 11 to 18 mol %, between 11 to 16 mol %, or between 11 to 15 mol %. Exemplary fining agents include, but are not limited to SnO₂ and Sb₂O₃ which can change the tilt of the respective transmission curve by improving red transmission and slightly decreasing blue transmission, as antimony affects the oxidation state of the system and thus changes the iron oxidation state which is the major driver for transmission.

In exemplary embodiments, ZnO can be used in a range of between 0 to 4 mol % but not in ZrO₂ containing glasses. ZrO₂ can be in the range of about 0 to 2 mol % or between 0 to 1.7 mol %. In other embodiments, Fe, Cr and Ni impurity levels must be kept low, on the order of <60 ppm total Fe, Cr and Ni and in other embodiments, <20 ppm total Fe, Cr and Ni. In some embodiments, the impurity levels should be Fe<20 ppm, Cr<5 ppm, and Ni<5 ppm. In further embodiments, other impurity levels for other coloring elements (e.g., Cu, V, Co, Mn, etc.) should be <20 ppm total.

Table 7 shows examples of glasses (samples 1-12) with high transmissibility as described herein.

TABLE 7 mol % 1 2 3 4 5 6 7 SiO2 75.64 75.71 75.71 75.47 76.84 75.20 74.51 B2O3 0.00 0.00 0.00 1.35 0.00 0.00 1.37 Al2O3 4.99 4.98 4.97 4.94 4.95 4.96 4.83 Na2O 1.91 0.94 0.90 0.95 0.94 0.96 0.94 K2O 3.01 3.99 5.01 4.89 4.93 4.98 4.81 MgO 3.23 3.23 2.99 2.97 2.97 3.35 3.00 CaO 2.90 2.88 2.66 3.08 3.05 3.44 3.03 SrO 3.36 3.34 3.09 3.10 3.08 3.47 4.11 BaO 3.33 3.31 3.05 3.10 3.10 3.49 1.94 SnO2 0.12 0.12 0.12 0.12 0.12 0.12 0.11 ZrO2 1.46 1.45 1.45 0.00 0.00 0.00 0.00 R2O 4.92 4.93 5.91 5.83 5.87 5.94 5.75 RO 12.83 12.76 11.80 12.26 12.20 13.75 12.08 Al2O3-R2O 0.07 0.05 −0.94 −0.89 −0.919 −0.99 −0.92 T(10^(∧)12P) [° C.] 752 766.5 760.5 711.2 730 725.4 713.9 T(anneal) [° C.] 710.9 724.3 718.7 670.1 688.2 684.5 673.3 T(strain) [° C.] 658.7 670.7 665.6 617.9 635.1 632.4 621.6 Density [g/cm³] 2.632 2.629 2.612 2.572 2.569 2.606 2.557 CTE [×10⁻⁷ 1/K] 55.6 55 59.1 60.9 61.7 63.9 61.2 T liq internal 72 h 1075 1075 1040 1025 1025 1035 1010 gradient [° C.] crystal Proto Proto Proto Diopside Diopside Diopside Diopside phase enstatite enstatite enstatite Viscosity Fulcher parameters A −2.3561 −2.5219 −2.5624 −1.9958 −2.1822 −2.1545 −2.1562 B 6588.95 6908.77 7112.80 6157.51 6632.70 6285.90 6447.66 T0 293.148 290.846 266.895 271.295 262.257 281.304 252.846 T(200 P) [° C.] 1708 1723 1729 1704 1742 1692 1699 T(400 P) [° C.] 1622 1639 1644 1611 1649 1603 1608 T(35 kP) [° C.] 1248 1269 1268 1213 1248 1220 1215 ΔT (200 P − 35 kP) [° C.] 460 455 462 492 493 472 484 Viscosity at T-liq [P] 1178400 1943700 4344400 1492300 3262900 1533100 2288000 Transmission (measured) % 450 nm 93.10 91.92 93.48 94.42 94.17 93.90 94.41 550 nm 93.85 92.82 94.01 94.90 94.49 94.15 94.35 630 nm 84.84 83.83 85.38 86.85 85.86 84.86 85.78 mol % 8 9 10 11 12 SiO2 75.71 75.40 76.54 74.20 75.14 B2O3 2.67 2.60 2.46 2.96 2.94 Al2O3 4.62 4.72 3.93 4.90 4.51 Na2O 0.95 0.97 0.96 0.06 0.04 K2O 4.76 3.90 4.84 5.89 5.95 MgO 3.02 3.03 3.01 3.18 2.67 CaO 3.04 3.06 3.03 2.74 4.00 SrO 3.09 4.17 3.08 3.66 3.08 BaO 2.00 1.99 1.99 2.28 1.53 SnO2 0.12 0.12 0.12 0.12 0.12 ZrO2 0.00 0.00 0.00 0.00 0.00 R2O 5.85 4.86 5.80 5.95 5.99 RO 11.23 12.23 11.14 11.85 11.27 Al2O3-R2O −1.24 −0.14 −1.87 −1.05 −1.48 T(10^(∧)12P) [° C.] 719.8 703 694.2 714.2 720 T(anneal) [° C.] 677.1 662.1 654.2 673.7 678.5 T(strain) [° C.] 622.9 610.3 603.4 622.2 625.8 Density [g/cm³] 2.525 2.546 2.526 2.55 2.513 CTE [×10⁻⁷ 1/K] 59.4 56.8 59.1 62.4 60.8 T liq internal 72 h 1020 1040 1005 1010 1025 gradient [° C.] crystal Diopside Diopside Diopside Diopside Strontium phase Silicate Viscosity Fulcher parameters A −1.8184 −2.2585 −2.2888 −1.8606 −1.7872 B 5947.28 6809.29 6802.91 5818.11 5701.58 T0 280.52 221.157 214.370 294.520 306.415 T(200 P) [° C.] 1724 1715 1697 1693 1701 T(400 P) [° C.] 1626 1622 1605 1598 1605 T(35 kP) [° C.] 1215 1222 1210 1203 1207 ΔT (200 P − 35 kP) [° C.] 509 492 487 490 494 Viscosity at T-liq [P] 1675500 1140800 2068600 1866900 1403500 Transmission (measured) % 450 nm 93.98 93.65 94.25 93.39 94.06 550 nm 94.94 94.46 95.06 94.37 95.16 630 nm 87.78 86.66 87.82 86.19 87.92

As noted in the above tables an exemplary glass article in some embodiments can comprise a glass sheet with a front face having a width and a height, a back face opposite the front face, and a thickness between the front face and back face, forming four edges around the front and back faces, wherein the glass sheet comprises between about 74 mol % to about 77 mol % SiO₂, between about 3 mol % to about 6 mol % Al₂O₃, between about 0 mol % to about 3.5 mol % B₂O₃, between about 4 mol % to about 7 mol % R₂O, wherein R is any one or more of Li, Na, K, Rb, Cs, between about 11 mol % to about 16 mol % RO, wherein R is any one or more of Mg, Ca, Sr or Ba, between about 0 mol % to about 4 mol % ZnO, and between about 0 mol % to about 1.7 mol % ZrO₂. In some embodiments, the glass has a color shift<0.005. In some embodiments, the glass has a strain temperature greater than about 600° C. In some embodiments, the glass has an annealing temperature greater than about 650° C. In some embodiments, the glass has a CTE between about 55×10−7/° C. and about 64×10−7/° C. In some embodiments, the glass has a density between about 2.51 gm/cc @ 20 C and about 2.64 gm/cc @ 20 C. In some embodiments, the glass article is a light guide plate. In some embodiments, the thickness of the plate is between about 0.2 mm and about 8 mm. In some embodiments, the light guide plate is manufactured from a fusion draw process, slot draw process, or a float process. In some embodiments, the glass comprises less than about 20 ppm each of Co, Ni, and Cr. In some embodiments, the glass comprises less than about 20 ppm total of Co, Ni, and Cr. In some embodiments, the glass comprises less than about 20 ppm of Fe, less than about 5 ppm of Co, and less than about 5 ppm of Ni. In some embodiments, Al₂O₃/R₂O<1. In some embodiments, Al₂O₃ is substantially equal to R₂O+/−0.05. In some embodiments, the glass does not contain BaO and the mol % of SrO, MgO and CaO are within 1.0 mol % of each other. In some embodiments, the glass contains BaO and the mol % of SrO, BaO, MgO and CaO are within 1.0 mol % of each other. In some embodiments, the T35 kP temperature is greater than or equal to 1200° C. In some embodiments, the T200 P temperature is less than or equal to 1700° C. In some embodiments, the transmittance at 450 nm with at least 500 mm in length is greater than or equal to 85%, the transmittance at 550 nm with at least 500 mm in length is greater than or equal to 90%, or the transmittance at 630 nm with at least 500 mm in length is greater than or equal to 85%, and combinations thereof. In some embodiments, the glass sheet is chemically strengthened. In some embodiments, R₂O/RO is between about 0.3 to less than about 1.0. In some embodiments, R₂O/RO is between about 0.38 to about 0.53. In some embodiments, Al₂O₃—R₂O is between −2 and 0.5.

In other embodiments, a glass article is provided comprising a glass sheet with a front face having a width and a height, a back face opposite the front face, and a thickness between the front face and back face, forming four edges around the front and back faces, wherein the glass sheet comprises greater than about 74 mol % SiO₂, between about 3 mol % to about 6 mol % Al₂O₃, between about 0 mol % to about 3.5 mol % B₂O₃, between about 4 mol % to about 7 mol % R₂O, wherein R is any one or more of Li, Na, K, Rb, Cs, wherein Al₂O₃—R₂O is between about −2 and about 0.5. In further embodiments, a glass article is provided comprising a glass sheet with a front face having a width and a height, a back face opposite the front face, and a thickness between the front face and back face, forming four edges around the front and back faces, wherein the glass sheet comprises greater than about 74 mol % SiO₂, between about 3 mol % to about 6 mol % Al₂O₃, between about 0 mol % to about 3.5 mol % B₂O₃, between about 4 mol % to about 7 mol % R₂O, wherein R is any one or more of Li, Na, K, Rb, Cs, between about 11 mol % to about 16 mol % RO, wherein R is any one or more of Mg, Ca, Sr or Ba, wherein R₂O/RO is between about 0.3 to less than about 1.0. In some embodiments, R₂O/RO is between about 0.38 to about 0.53. In some embodiments, the glass has a color shift<0.005. In some embodiments, the glass has a strain temperature greater than about 600° C. In some embodiments, the glass has an annealing temperature greater than about 650° C. In some embodiments, the glass has a CTE between about 55×10−7/° C. and about 64×10−7/° C. In some embodiments, the glass has a density between about 2.51 gm/cc @ 20 C and about 2.64 gm/cc @ 20 C. In some embodiments, the glass article is a light guide plate. In some embodiments, the thickness of the plate is between about 0.2 mm and about 8 mm. In some embodiments, the light guide plate is manufactured from a fusion draw process, slot draw process, or a float process. In some embodiments, the glass comprises less than about 20 ppm each of Co, Ni, and Cr. In some embodiments, the glass comprises less than about 20 ppm total of Co, Ni, and Cr. In some embodiments, the glass comprises less than about 20 ppm of Fe, less than 5 ppm of Co, and less than 5 ppm of Ni. In some embodiments, Al₂O₃/R₂O<1. In some embodiments, Al₂O₃ is substantially equal to R₂O+/−0.05. In some embodiments, the transmittance at 450 nm with at least 500 mm in length is greater than or equal to 85%, the transmittance at 550 nm with at least 500 mm in length is greater than or equal to 90%, or the transmittance at 630 nm with at least 500 mm in length is greater than or equal to 85%, and combinations thereof.

In yet further embodiments, a glass article is provided comprising a glass sheet with a front face having a width and a height, a back face opposite the front face, and a thickness between the front face and back face, forming four edges around the front and back faces, wherein the glass sheet comprises greater than about 74 mol % SiO₂, between about 3 mol % to about 6 mol % Al₂O₃, between about 0 mol % to about 3.5 mol % B₂O₃, between about 4 mol % to about 7 mol % R₂O, wherein R is any one or more of Li, Na, K, Rb, Cs, between about 11 mol % to about 16 mol % RO, wherein R is any one or more of Mg, Ca, Sr or Ba, wherein Al₂O₃—R₂O is between about −2 and about 0.5, and wherein R₂O/RO is between about 0.3 to less than about 1.0. In some embodiments, R₂O/RO is between about 0.38 to about 0.53. In some embodiments, the glass has a color shift<0.005. In some embodiments, the glass article is a light guide plate. In some embodiments, the glass comprises less than about 20 ppm each of Co, Ni, and Cr. In some embodiments, the glass comprises less than about 20 ppm total of Co, Ni, and Cr. In some embodiments, the glass comprises less than about 20 ppm of Fe, less than 5 ppm of Co, and less than 5 ppm of Ni.

It will be appreciated that the various disclosed embodiments may involve particular features, elements or steps that are described in connection with that particular embodiment. It will also be appreciated that a particular feature, element or step, although described in relation to one particular embodiment, may be interchanged or combined with alternate embodiments in various non-illustrated combinations or permutations.

It is also to be understood that, as used herein the terms “the,” “a,” or “an,” mean “at least one,” and should not be limited to “only one” unless explicitly indicated to the contrary. Thus, for example, reference to “a ring” includes examples having two or more such rings unless the context clearly indicates otherwise. Likewise, a “plurality” or an “array” is intended to denote “more than one.” As such, a “plurality of droplets” includes two or more such droplets, such as three or more such droplets, etc., and an “array of rings” comprises two or more such droplets, such as three or more such rings, etc.

Ranges can be expressed herein as from “about” one particular value, and/or to “about” another particular value. When such a range is expressed, examples include from the one particular value and/or to the other particular value. Similarly, when values are expressed as approximations, by use of the antecedent “about,” it will be understood that the particular value forms another aspect. It will be further understood that the endpoints of each of the ranges are significant both in relation to the other endpoint, and independently of the other endpoint.

The terms “substantial,” “substantially,” and variations thereof as used herein are intended to note that a described feature is equal or approximately equal to a value or description. For example, a “substantially planar” surface is intended to denote a surface that is planar or approximately planar. Moreover, as defined above, “substantially similar” is intended to denote that two values are equal or approximately equal. In some embodiments, “substantially similar” may denote values within about 10% of each other, such as within about 5% of each other, or within about 2% of each other.

Unless otherwise expressly stated, it is in no way intended that any method set forth herein be construed as requiring that its steps be performed in a specific order. Accordingly, where a method claim does not actually recite an order to be followed by its steps or it is not otherwise specifically stated in the claims or descriptions that the steps are to be limited to a specific order, it is no way intended that any particular order be inferred.

While various features, elements or steps of particular embodiments may be disclosed using the transitional phrase “comprising,” it is to be understood that alternative embodiments, including those that may be described using the transitional phrases “consisting” or “consisting essentially of,” are implied. Thus, for example, implied alternative embodiments to a device that comprises A+B+C include embodiments where a device consists of A+B+C and embodiments where a device consists essentially of A+B+C.

It will be apparent to those skilled in the art that various modifications and variations can be made to the present disclosure without departing from the spirit and scope of the disclosure. Since modifications combinations, sub-combinations and variations of the disclosed embodiments incorporating the spirit and substance of the disclosure may occur to persons skilled in the art, the disclosure should be construed to include everything within the scope of the appended claims and their equivalents. 

What is claimed is:
 1. A glass article, comprising: a glass sheet with a front face having a width and a height, a back face opposite the front face, and a thickness between the front face and back face, forming four edges around the front and back faces, wherein the glass sheet comprises: between about 74 mol % to about 77 mol % SiO₂, between about 3 mol % to about 6 mol % Al₂O₃, between about 0 mol % to about 3.5 mol % B₂O₃, between about 4 mol % to about 7 mol % R₂O, wherein R is any one or more of Li, Na, K, Rb, Cs, between about 11 mol % to about 16 mol % RO, wherein R is any one or more of Mg, Ca, Sr or Ba, between about 0 mol % to about 4 mol % ZnO, and between about 0 mol % to about 1.7 mol % ZrO₂, wherein RO satisfies a compositional relationship selected from the group consisting of: (a) the glass contains BaO and the mol % of SrO, BaO, MgO, and CaO are within 1.0 mol % of each other; and (b) the glass does not contain BaO and the mol % of SrO, MgO, and CaO are within 1.0 mol % of each other.
 2. The glass article of claim 1, wherein the glass has a color shift <0.005.
 3. The glass article of claim 1, wherein the glass has a strain temperature greater than about 600° C.
 4. The glass article of claim 1, wherein the glass has an annealing temperature greater than about 650° C.
 5. The glass article of claim 1, wherein the glass has a CTE between about 55×10⁻⁷/° C. and about 64×10⁻⁷/° C.
 6. The glass article of claim 1, wherein the glass has a density between about 2.51 gm/cc @ 20° C. and about 2.64 gm/cc @ 20° C.
 7. The glass article of claim 1, wherein the glass article is a light guide plate.
 8. The glass article of claim 7, wherein the thickness of the plate is between about 0.2 mm and about 8 mm.
 9. The glass article of claim 7, wherein the light guide plate is manufactured from a fusion draw process, slot draw process, or a float process.
 10. The glass article of claim 1, wherein the glass comprises less than about 20 ppm each of Co, Ni, and Cr.
 11. The glass article of claim 1, wherein the glass comprises less than about 20 ppm total of Co, Ni, and Cr.
 12. The glass article of claim 1, wherein the glass comprises less than about 20 ppm of Fe, less than about 5 ppm of Co, and less than about 5 ppm of Ni.
 13. The glass article of claim 1, wherein Al₂O₃/R₂O<1.
 14. The glass article of claim 1, wherein Al₂O₃ is substantially equal to R₂O+/−0.05.
 15. The glass article of claim 1, wherein the T35 kP temperature is greater than or equal to 1200° C.
 16. The glass article of claim 1, wherein the T200P temperature is less than or equal to 1700° C.
 17. The glass article of claim 1 wherein the transmittance at 450 nm with at least 500 mm in length is greater than or equal to 85%, the transmittance at 550 nm with at least 500 mm in length is greater than or equal to 90%, or the transmittance at 630 nm with at least 500 mm in length is greater than or equal to 85%, and combinations thereof.
 18. The glass article of claim 1 wherein the glass sheet is chemically strengthened.
 19. The glass article of claim 1 wherein R₂O/RO is between about 0.3 to less than about 1.0.
 20. The glass article of claim 1 wherein R₂O/RO is between about 0.38 to about 0.53.
 21. The glass article of claim 1 wherein Al₂O₃— R₂O is between −2 and 0.5.
 22. A glass article, comprising: a glass sheet with a front face having a width and a height, a back face opposite the front face, and a thickness between the front face and back face, forming four edges around the front and back faces, wherein the glass sheet comprises: greater than about 74 mol % SiO₂, between about 3 mol % to about 6 mol % Al₂O₃, between about 0 mol % to about 3.5 mol % B₂O₃, between about 4 mol % to about 7 mol % R₂O, wherein R is any one or more of Li, Na, K, Rb, Cs, between about 10 mol % to about 20 mol % RO, wherein R is any one or more of Mg, Ca, Sr or Ba, wherein: Al₂O₃—R₂O is between about −2 and about 0.5, and RO satisfies a compositional relationship selected from the group consisting of: (a) the glass contains BaO and the mol % of SrO, BaO, MgO, and CaO are within 1.0 mol % of each other; and (b) the glass does not contain BaO and the mol % of SrO, MgO, and CaO are within 1.0 mol % of each other.
 23. A glass article, comprising: a glass sheet with a front face having a width and a height, a back face opposite the front face, and a thickness between the front face and back face, forming four edges around the front and back faces, wherein the glass sheet comprises: greater than about 74 mol % SiO₂, between about 3 mol % to about 6 mol % Al₂O₃, between about 0 mol % to about 3.5 mol % B₂O₃, between about 4 mol % to about 7 mol % R₂O, wherein R is any one or more of Li, Na, K, Rb, Cs, between about 11 mol % to about 16 mol % RO, wherein R is any one or more of Mg, Ca, Sr or Ba, wherein: R₂O/RO is between about 0.3 to less than about 1.0, and RO satisfies a compositional relationship selected from the group consisting of: (a) the glass contains BaO and the mol % of SrO, BaO, MgO, and CaO are within 1.0 mol % of each other; and (b) the glass does not contain BaO and the mol % of SrO, MgO, and CaO are within 1.0 mol % of each other.
 24. The glass article of any of claims 22-23 wherein R₂O/RO is between about 0.38 to about 0.53.
 25. The glass article of any of claims 22-23, wherein the glass has a color shift <0.005.
 26. The glass article of any of claims 22-23, wherein the glass has a strain temperature greater than about 600° C.
 27. The glass article of any of claims 22-23, wherein the glass has an annealing temperature greater than about 650° C.
 28. The glass article of any of claims 22-23, wherein the glass has a CTE between about 55×10⁻⁷/° C. and about 64×10⁻⁷/° C.
 29. The glass article of any of claims 22-23, wherein the glass has a density between about 2.51 gm/cc @ 20° C. and about 2.64 gm/cc @ 20° C.
 30. The glass article of any of claims 22-23, wherein the glass article is a light guide plate.
 31. The glass article of claim 30, wherein the thickness of the plate is between about 0.2 mm and about 8 mm.
 32. The glass article of claim 30, wherein the light guide plate is manufactured from a fusion draw process, slot draw process, or a float process.
 33. The glass article of any of claims 22-23, wherein the glass comprises less than about 20 ppm each of Co, Ni, and Cr.
 34. The glass article of any of claims 22-23, wherein the glass comprises less than about 20 ppm total of Co, Ni, and Cr.
 35. The glass article of any of claims 22-23, wherein the glass comprises less than about 20 ppm of Fe, less than 5 ppm of Co, and less than 5 ppm of Ni.
 36. The glass article of any of claims 22-23, wherein Al₂O₃/R₂O<1.
 37. The glass article of any of claims 22-23, wherein Al₂O₃ is substantially equal to R₂O+/−0.05.
 38. The glass article of any of claims 22-23, wherein the transmittance at 450 nm with at least 500 mm in length is greater than or equal to 85%, the transmittance at 550 nm with at least 500 mm in length is greater than or equal to 90%, or the transmittance at 630 nm with at least 500 mm in length is greater than or equal to 85%, and combinations thereof.
 39. A glass article, comprising: a glass sheet with a front face having a width and a height, a back face opposite the front face, and a thickness between the front face and back face, forming four edges around the front and back faces, wherein the glass sheet comprises: greater than about 74 mol % SiO₂, between about 3 mol % to about 6 mol % Al₂O₃, between about 0 mol % to about 3.5 mol % B₂O₃, between about 4 mol % to about 7 mol % R₂O, wherein R is any one or more of Li, Na, K, Rb, Cs, between about 11 mol % to about 16 mol % RO, wherein R is any one or more of Mg, Ca, Sr or Ba, wherein: Al₂O₃—R₂O is between about −2 and about 0.5, R₂O/RO is between about 0.3 to less than about 1.0, and RO satisfies a compositional relationship selected from the group consisting of: (a) the glass contains BaO and the mol % of SrO, BaO, MgO, and CaO are within 1.0 mol % of each other; and (b) the glass does not contain BaO and the mol % of SrO, MgO, and CaO are within 1.0 mol % of each other.
 40. The glass article of claim 39 wherein R₂O/RO is between about 0.38 to about 0.53.
 41. The glass article of claim 39, wherein the glass has a color shift <0.005.
 42. The glass article of claim 39, wherein the glass article is a light guide plate.
 43. The glass article of claim 39, wherein the glass comprises less than about 20 ppm each of Co, Ni, and Cr.
 44. The glass article of claim 39, wherein the glass comprises less than about 20 ppm total of Co, Ni, and Cr.
 45. The glass article of claim 39, wherein the glass comprises less than about 20 ppm of Fe, less than 5 ppm of Co, and less than 5 ppm of Ni. 